CN115821167A - Ultrahigh-strength saddle plate and manufacturing method thereof - Google Patents
Ultrahigh-strength saddle plate and manufacturing method thereof Download PDFInfo
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- 238000010438 heat treatment Methods 0.000 claims abstract description 34
- 238000010791 quenching Methods 0.000 claims abstract description 33
- 230000000171 quenching effect Effects 0.000 claims abstract description 33
- 238000001816 cooling Methods 0.000 claims abstract description 23
- 229910000831 Steel Inorganic materials 0.000 claims abstract description 18
- 239000010959 steel Substances 0.000 claims abstract description 18
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims abstract description 15
- 238000003723 Smelting Methods 0.000 claims abstract description 14
- 239000002994 raw material Substances 0.000 claims abstract description 14
- 230000006698 induction Effects 0.000 claims abstract description 13
- 239000000463 material Substances 0.000 claims abstract description 8
- 238000005266 casting Methods 0.000 claims abstract description 7
- 238000003756 stirring Methods 0.000 claims abstract description 7
- 229910052742 iron Inorganic materials 0.000 claims abstract description 6
- 238000005520 cutting process Methods 0.000 claims abstract description 5
- 238000000265 homogenisation Methods 0.000 claims abstract description 5
- 239000011261 inert gas Substances 0.000 claims abstract description 5
- 238000005096 rolling process Methods 0.000 claims abstract description 5
- 239000002245 particle Substances 0.000 claims description 32
- 238000000034 method Methods 0.000 claims description 17
- 238000004321 preservation Methods 0.000 claims description 8
- 238000005204 segregation Methods 0.000 claims description 4
- 230000000694 effects Effects 0.000 abstract description 4
- 239000013078 crystal Substances 0.000 description 12
- 229910000734 martensite Inorganic materials 0.000 description 11
- 230000000052 comparative effect Effects 0.000 description 10
- 238000012546 transfer Methods 0.000 description 10
- 229910001566 austenite Inorganic materials 0.000 description 8
- MCMNRKCIXSYSNV-UHFFFAOYSA-N Zirconium dioxide Chemical compound O=[Zr]=O MCMNRKCIXSYSNV-UHFFFAOYSA-N 0.000 description 6
- 239000010419 fine particle Substances 0.000 description 5
- 238000005728 strengthening Methods 0.000 description 5
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- VWZIXVXBCBBRGP-UHFFFAOYSA-N boron;zirconium Chemical compound B#[Zr]#B VWZIXVXBCBBRGP-UHFFFAOYSA-N 0.000 description 1
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Abstract
The application relates to the technical field of automobile traction components, and particularly discloses an ultrahigh-strength saddle plate and a manufacturing method thereof, wherein the ultrahigh-strength saddle plate comprises the following raw materials in percentage by mass: 0.15 to 0.35 percent of C, 1.0 to 1.8 percent of Mn, less than or equal to 0.5 percent of Si, less than or equal to 0.005 percent of B, 0.0015 to 0.035 percent of Zr, 0.15 to 0.2 percent of Al, zrB 2 0.002‑0.007%，ZrO 2 0.001-0.004%, and the balance of iron; the manufacturing method comprises the following steps: step one, smelting: uniformly stirring the raw materials in a vacuum induction furnaceSmelting and casting into a steel plate; step two, homogenization treatment: heating the steel plate under the protection of inert gas, preserving heat, cooling to normal temperature in air, rolling to the required material thickness, and cutting into part blanks; step three, hot stamping and forming: and D, firstly, performing cold stamping on the blank obtained in the step two by using a performing die, then quickly moving the blank into the die for stamping, maintaining the pressure and quenching to obtain the saddle plate. It has the effect of obtaining the saddle board of superhigh strength when guaranteeing the lightweight.
Description
Technical Field
The invention relates to the technical field of automobile traction components, in particular to an ultrahigh-strength saddle plate and a manufacturing method thereof.
Background
The saddle plate is a connecting device arranged between a tractor frame and a saddle and is used for connecting the saddle and the tractor frame into a whole and then connecting the saddle and a trailer to realize the connection of the semitrailer main vehicle and the trailer.
In the related art, saddle plates are generally made of low-strength steel, which is thickened to achieve the desired final properties; when the saddle plate is produced by using high-strength steel, the problems of resilience, wrinkles, cracking and the like are easily caused on the whole body when the saddle plate is bent. Therefore, with the fierce competition of light weight of automobile in the market, the saddle plate needs to have ultrahigh strength and ensure light weight, a balance point needs to be found between high strength and light weight, and the balance point is a difficult point facing at present.
Disclosure of Invention
In order to obtain the saddle plate of superhigh strength while guaranteeing lightweight, this application provides a saddle plate of superhigh strength and manufacturing method thereof.
The application provides an ultra-high strength saddle plate and a manufacturing method thereof, which adopts the following technical scheme:
the ultra-high strength saddle plate comprises the following raw materials in percentage by mass: 0.15 to 0.35 percent of C, 1.0 to 1.8 percent of Mn, less than or equal to 0.5 percent of Si, less than or equal to 0.005 percent of B, and the balance of Fe.
By adopting the technical scheme, the reasonable Mn element content is adopted, and Si and B are compositely added as important alloy elements in cooperation with the C element content. C. Mn is a solid solution strengthening element, can improve the strength of the steel, has low Mn content, and the steelThe strength of the plate is not enough, the plate is not beneficial to later-stage forming, mn element can improve hardenability by reducing phase change driving force, the martensite ratio can be effectively improved, and the strength is obviously improved; the radius of Si atoms is larger than that of Fe, si can be dissolved in austenite in a solid mode, the wear resistance can be improved, reasonable addition amount of B can ensure that the hardenability and the strength of steel are selectable, and the saddle plate comprises the following raw materials in percentage by mass: 0.2 to 0.28 percent of C, 1.3 to 1.5 percent of Mn, 0.3 percent of Si, 0.005 percent of B, 0.0017 to 0.02 percent of Zr, 0.17 to 0.2 percent of Al, and ZrB 2 0.004-0.006％，ZrO 2 0.001-0.003% of iron as the rest.
By adopting the technical scheme, the saddle plate is prepared by adopting the raw materials of the components, in the manufacturing process of the saddle plate, in the stage that austenite crystal grains do not grow, a refined martensite structure is obtained by quenching, and the saddle plate with high strength and hardness can be obtained by the more refined martensite structure. However, high temperature makes austenite grains larger because the growth stage of austenite grains cannot be precisely controlled, and a finer martensite structure cannot be accurately obtained.
By adding Zr and Al metal, higher strength and hardenability can be obtained, and the plasticity is good during cold deformation. ZrB with high melting point, high hardness, high chemical stability and lower density is adopted 2 ，ZrB 2 The fine particles are distributed in the crystal phase to play a role of dispersion strengthening, so that the strength of the material is increased.
By adding a proper amount of nano ZrO 2 Particles, zrO of fine particle size 2 The grain boundary is increased by the particles, dislocation movement is greatly hindered when external force acts, and fine ZrO is formed in the quenching stage 2 The particles can block the movement of the crystal boundary, thereby inhibiting the excessive growth of the crystal grains and playing a role in refining the crystal grains. Further, zrO 2 Can improve the effect of adding ZrB 2 The problem of increased sheet toughness is caused, and the dual functions of grain refinement and dispersion strengthening are realized, so that the saddle plate has ultrahigh strength.
Optionally, the ZrB 2 The particle size is 20-35nm.
By adopting the technical scheme, zrB is added 2 Particles, acting as age-hardening, zrB 2 The fine particles are distributed in a crystal phase, the finer the particles are, the more the crystal boundaries are generated, the same deformation amount can be dispersed into more crystal boundaries during phase change, and the more uniform deformation can be generated without causing excessive concentration of local stress, so that the strength of the material is improved.
Optionally, the ZrO 2 The particle size is 40-50nm.
By adopting the technical scheme, zrO with fine grain size 2 The grains increase the grain boundary, and when an external force acts, the dislocation movement is hindered to be enlarged, so that the excessive growth of the grains is inhibited, the martensite is refined, and the strength of the saddle plate is increased.
In a second aspect, the present application provides a method for manufacturing an ultra-high strength saddle plate, which adopts the following technical solution:
a manufacturing method of an ultra-high strength saddle plate comprises the following steps:
step one, smelting: uniformly stirring and smelting the raw materials in a vacuum induction furnace, and then casting the raw materials into a steel plate;
step two, homogenization treatment: heating the steel plate to 1100-1150 ℃ in a heating furnace under the protection of inert gas, preserving heat for 1.5-2.5h, cooling to normal temperature in air, eliminating component segregation, rolling to the required material thickness, and cutting into part blanks;
step three, hot stamping and forming: and D, firstly, carrying out cold stamping on the blank obtained in the step two by using a pre-forming die, stamping the blank into the shape of the saddle plate part, then heating and preserving heat in the furnace, then quickly moving the saddle plate into the die for stamping, maintaining the pressure and quenching to obtain the saddle plate.
Through adopting above-mentioned technical scheme, with the low strength blank under the normal atmospheric temperature, heat to austenitizing temperature to keep warm a period, make it even austenitizing, then quick stamping forming in the hot forming die that has cooling system to transfer to inside fast, under certain pressurize pressure, carry out quenching in the mould and handle, pressurize quenching a period makes austenite structure change into martensite structure, in order to obtain the saddle board of lightweight superhigh strength.
Optionally, in the third step, the heating temperature in the furnace is 900-950 ℃, and the heat preservation time is 3-10min.
By adopting the technical scheme, the heating temperature and the heat preservation time are necessary conditions for realizing uniform austenitization of the blank, the heat preservation time is defined as soaking time of the blank in a furnace after the blank reaches the specified heating temperature, the length of the heat preservation time can influence whether a uniform structure can be obtained, the heating temperature is kept above the recrystallization temperature of the blank to ensure the austenitization of the blank, the crystal grain size of is gradually increased along with the extension of the heat preservation time, and then the growth trend of the crystal grains is gradually slowed down. In order to ensure that fine and uniform austenite grains are obtained, it is necessary to avoid coarsening of grains caused by long-term heating.
Optionally, the cooling rate of quenching in the third step is 20-30 ℃/s.
By adopting the technical scheme, the hot stamping not only ensures the forming in the die at high temperature, but also ensures enough quenching and cooling rate so as to form a martensite structure, and the larger the cooling rate of the blank, the easier the blank is quenched. But huge quenching stress is easily generated inside the hot stamping die to cause deformation and cracking, and the determination of the cooling rate parameter suitable for the hot stamping process is a necessary condition for ensuring the process quality of a hot stamping product and the performance of a final product.
Optionally, the saddle plate has a final thickness of 1-4mm.
By adopting the technical scheme, the thinner the thickness of the hot stamping product is, the lower the unit area crack expansion energy and the tearing strength are, and the nano ZrO is added 2 And ZrB 2 The presence of a large number of dislocations in the particles during the austenite to martensite phase transformation is hindered by the particles, so that cracks are not easily generated and high strength is maintained.
In summary, the present application has the following beneficial effects:
1. because the application adds ZrB 2 Nanoparticles of ZrB with high melting point, high hardness, high chemical stability and lower density 2 ，ZrB 2 The fine particles are distributed in the crystal phase to play a role of dispersion strengthening, so that the strength of the material is increased.
2. Addition of nano-ZrO in the present application 2 Particles of, zrO 2 The grain boundary is increased by the particles, dislocation movement is greatly hindered when external force acts, and fine ZrO is formed in the quenching stage 2 The particles can block the movement of the grain boundary, thereby inhibiting the excessive growth of the grains and playing a role in refining the grains.
3. The method heats the blank with low strength at normal temperature to austenitizing temperature, preserves heat for a period of time, makes the blank austenitizing uniform, then quickly transfers the blank to rapid punch forming in a thermal forming die with a cooling system inside, and carries out quenching treatment in the die under certain pressure maintaining pressure, and the pressure maintaining quenching is carried out for a period of time, so that austenite tissues are changed into martensite tissues to obtain the saddle plate with ultrahigh strength.
Detailed Description
Embodiment of manufacturing method of ultra-high strength saddle plate
Example 1
A manufacturing method of an ultra-high strength saddle plate comprises the following steps:
step one, smelting: sequentially adding the components of C, mn, si, B and Fe into a vacuum induction furnace, uniformly stirring and smelting for 50min in the vacuum induction furnace at 1300 ℃, and then casting into a steel plate;
step two, homogenization treatment: heating the steel plate to 1100-1150 ℃ in a heating furnace under the protection of inert gas, preserving heat for 2h, cooling to normal temperature in air, eliminating component segregation, rolling to the required material thickness, and cutting into part blanks;
step three, hot stamping and forming: and D, performing cold stamping on the blank obtained in the step two by using a preforming die, stamping the blank into a shape approximate to that of a saddle plate part, and heating in a furnace at the heating temperature of 925 ℃ for 5min to fully austenitize the blank. And then rapidly moving the saddle plate into a die for stamping, pressure maintaining and quenching, wherein the transfer time is 5s, the stamping pressure is 480T, the pressure maintaining pressure is 1010T, the pressure maintaining time is 18s, quenching treatment is carried out at the cooling rate of 25 ℃/s, the saddle plate is taken out when the saddle plate is cooled to be below 250 ℃, and the thickness of the saddle plate is 3mm finally.
Example 2
A manufacturing method of an ultra-high strength saddle plate comprises the following steps:
step one, smelting: mixing C, mn, si, B, zr, al and ZrB 2 ，ZrO 2 The Fe components are sequentially added into a vacuum induction furnace, uniformly stirred and smelted for 50min in the vacuum induction furnace at 1300 ℃, and then cast into a steel plate, wherein ZrB 2 ZrO particle size of 30nm 2 The grain diameter is 45nm;
step two, homogenization treatment: heating the steel plate to 1100-1150 ℃ in a heating furnace under the protection of inert gas, preserving heat for 2h, cooling to normal temperature in air, eliminating component segregation, rolling to the required material thickness, and cutting into part blanks;
step three, hot stamping and forming: and D, firstly, carrying out cold stamping on the blank obtained in the step two by using a pre-forming die, stamping the blank into a shape which is approximately like a saddle plate part, and then heating the blank in a furnace at the heating temperature of 925 ℃ for 5min so as to fully austenitize the blank. And then rapidly moving the saddle plate into a die for stamping, pressure maintaining and quenching, wherein the transfer time is 5s, the stamping pressure is 480T, the pressure maintaining pressure is 1010T, the pressure maintaining time is 18s, quenching treatment is carried out at the cooling rate of 25 ℃/s, the saddle plate is taken out when the saddle plate is cooled to be below 250 ℃, and the thickness of the saddle plate is 3mm finally.
Example 3
A method for manufacturing an ultra-high strength saddle plate, which is different from embodiment 1 in that ZrB 2 Particle size of 20nm, zrO 2 The particle size is 40nm, and the specific steps of the third step are as follows: and D, firstly, carrying out cold stamping on the blank obtained in the step two by using a preforming die, stamping the blank into a shape approximate to that of the saddle plate part, and then heating the blank in a furnace at the heating temperature of 900 ℃ for 3min so as to fully austenitize the blank. And then rapidly moving the saddle to a die for stamping, pressure maintaining and quenching, wherein the transfer time is 5s, the stamping pressure is 480T, the pressure maintaining pressure is 1010T, the pressure maintaining time is 18s, quenching treatment is carried out at a cooling rate of 20 ℃/s, and the saddle is taken out when the saddle is cooled to below 250 ℃ to obtain the saddle plate, and the thickness of the saddle plate is 3mm finally.
Example 4
A manufacturing method of an ultra-high strength saddle plate is different from that of embodiment 1 in that ZrB is used 2 ZrO particle size of 35nm 2 The particle size is 50nm, and the specific steps of the third step are as follows: and D, firstly, carrying out cold stamping on the blank obtained in the step two by using a pre-forming die, stamping the blank into a shape which is approximately like a saddle plate part, and then heating the blank in a furnace at 950 ℃ for 10min to fully austenitize the blank. And then rapidly moving the saddle plate into a die for stamping, pressure maintaining and quenching, wherein the transfer time is 5s, the stamping pressure is 480T, the pressure maintaining pressure is 1010T, the pressure maintaining time is 18s, quenching treatment is carried out at the cooling rate of 30 ℃/s, the saddle plate is taken out when the saddle plate is cooled to be below 250 ℃, and the thickness of the saddle plate is 3mm finally.
The raw material components and their corresponding parts by mass of examples 1-4 are shown in table 1.
Table 1 components and parts by mass (wt%) thereof in examples 1 to 4
| Components | Example 1 | Example 2 | Example 3 | Example 4 |
| C | 0.24 | 0.2 | 0.15 | 0.35 |
| Mn | 1.35 | 1.5 | 1.0 | 1.8 |
| Si | 0.37 | 0.3 | 0.5 | 0.27 |
| B | 0.0031 | 0.002 | 0.005 | 0.003 |
| Zr | — | 0.0019 | 0.0015 | 0.035 |
| Al | — | 0.01 | 0.2 | 0.15 |
| ZrB2 | — | 0.004 | 0.007 | 0.002 |
| ZrO2 | — | 0.002 | 0.001 | 0.004 |
| Fe | 98.0369 | 97.9801 | 98.1355 | 97.386 |
Example 5
A method for manufacturing an ultra-high strength saddle plate, which is different from embodiment 3 in that ZrB 2 The particle size was 18nm.
Example 6
A method for manufacturing an ultra-high strength saddle plate, which is different from embodiment 4 in that ZrB 2 The particle size was 40nm.
Example 7
A method for manufacturing an ultra-high strength saddle plate, which is different from embodiment 3 in that ZrO2 is used 2 The particle size was 35nm.
Example 8
A method for manufacturing an ultra-high strength saddle plate, which is different from embodiment 4 in that ZrO2 is used 2 The particle size was 55nm.
Example 9
The manufacturing method of the ultra-high strength saddle plate is different from the embodiment 3 in that the heating temperature in the third step is 850 ℃, the heat preservation time is 2min, and the specific steps in the third step are as follows:
and D, firstly, carrying out cold stamping on the blank obtained in the step two by using a pre-forming die, stamping the blank into a shape which is approximately like a saddle plate part, and then heating the blank in a furnace at the heating temperature of 850 ℃ for 2min so as to fully austenitize the blank. And then rapidly moving the saddle to a die for stamping, pressure maintaining and quenching, wherein the transfer time is 5s, the stamping pressure is 480T, the pressure maintaining pressure is 1010T, the pressure maintaining time is 18s, quenching treatment is carried out at a cooling rate of 20 ℃/s, and the saddle is taken out when the saddle is cooled to below 250 ℃ to obtain the saddle plate, and the thickness of the saddle plate is 3mm finally.
Example 10
The manufacturing method of the ultra-high strength saddle plate is different from the embodiment 4 in that the heating temperature in the third step is 980 ℃, the heat preservation time is 12min, and the specific steps in the third step are as follows:
and D, firstly, carrying out cold stamping on the blank obtained in the step two by using a pre-forming die, stamping the blank into a shape which is approximately like a saddle plate part, and then heating the blank in a furnace at 980 ℃ for 12min to fully austenitize the blank. And then rapidly moving the saddle plate into a die for stamping, pressure maintaining and quenching, wherein the transfer time is 5s, the stamping pressure is 480T, the pressure maintaining pressure is 1010T, the pressure maintaining time is 18s, quenching treatment is carried out at the cooling rate of 30 ℃/s, the saddle plate is taken out when the saddle plate is cooled to be below 250 ℃, and the thickness of the saddle plate is 3mm finally.
Example 11
A manufacturing method of an ultra-high strength saddle plate is different from embodiment 3 in that the cooling rate of quenching in the third step is 15 ℃/s, and the specific steps in the third step are as follows:
and D, firstly, carrying out cold stamping on the blank obtained in the step two by using a preforming die, stamping the blank into a shape approximate to that of the saddle plate part, and then heating the blank in a furnace at the heating temperature of 900 ℃ for 3min so as to fully austenitize the blank. And then quickly moving the saddle to a die for stamping, pressure maintaining and quenching, wherein the transfer time is 5s, the stamping pressure is 480T, the pressure maintaining pressure is 1010T, the pressure maintaining time is 18s, quenching treatment is carried out at a cooling rate of 15 ℃/s, and the saddle is taken out when the saddle is cooled to below 250 ℃ to obtain a saddle plate, and finally the thickness of the saddle plate is 3mm.
Example 12
The manufacturing method of the ultra-high strength saddle plate is different from the embodiment 4 in that the cooling rate of quenching in the third step is 35 ℃/s, and the concrete steps of the third step are as follows:
and D, firstly, performing cold stamping on the blank obtained in the step two by using a preforming die, stamping the blank into a shape approximate to that of a saddle plate part, and heating in a furnace at 950 ℃ for 10min to fully austenitize the blank. And then rapidly moving the saddle plate into a die for stamping, pressure maintaining and quenching, wherein the transfer time is 5s, the stamping pressure is 480T, the pressure maintaining pressure is 1010T, the pressure maintaining time is 18s, quenching treatment is carried out at the cooling rate of 35 ℃/s, the saddle plate is taken out when the saddle plate is cooled to be below 250 ℃, and the thickness of the saddle plate is 3mm finally.
Comparative example
Comparative example 1
A method for manufacturing an ultra-high strength saddle plate, which is different from embodiment 2 in that ZrB is not included as a raw material 2 The specific steps of the first step are as follows:
step one, smelting: sequentially adding C, mn, si, B, zr, al, zrO2 and Fe into a vacuum induction furnace, uniformly stirring and smelting in the vacuum induction furnace at 1300 ℃ for 50min, and then casting into a steel plate, wherein ZrO is 2 The particle size was 45nm.
Comparative example 2
A method for manufacturing an ultra-high strength saddle plate, which is different from embodiment 2 in that the raw material does not contain ZrO 2 The specific steps of the first step are as follows:
step one, smelting: sequentially adding C, mn, si, B, zr, al, zrB2 and Fe into a vacuum induction furnace, uniformly stirring and smelting in the vacuum induction furnace at 1300 ℃ for 50min, and then casting into a steel plate, wherein ZrB 2 The particle size was 30nm.
Comparative example 3
A method for manufacturing an ultra-high strength saddle plate, which is different from embodiment 2 in that the raw material does not contain ZrO 2 And ZrB 2 The specific steps of the first step are as follows:
step one, smelting: sequentially adding the components of C, mn, si, B, zr, al and Fe into a vacuum induction furnace, uniformly stirring and smelting for 50min in the vacuum induction furnace at 1300 ℃, and then casting into a steel plate.
Performance test
Experimental samples: the performance tests were carried out using the saddle plate samples prepared in examples 1 to 12 and comparative examples 1 to 3.
The experimental method comprises the following steps: the tensile strength (MPa), yield strength (MPa) and elongation (%) were measured according to GB/T228.1-2010 "tensile test for Metal materials".
TABLE 2 Performance test results
| Tensile Strength (MPa) | Yield strength (MPa) | Elongation (%) | |
| Example 1 | 1200 | 1000 | 6 |
| Example 2 | 1800 | 1300 | 8 |
| Example 3 | 1600 | 1200 | 7 |
| Example 4 | 1400 | 1100 | 6 |
| Example 5 | 1100 | 900 | 5 |
| Example 6 | 1050 | 850 | 6 |
| Example 7 | 1386 | 800 | 6 |
| Example 8 | 1000 | 840 | 4 |
| Example 9 | 970 | 610 | 4 |
| Example 10 | 951 | 790 | 5 |
| Example 11 | 896 | 680 | 5 |
| Example 12 | 854 | 600 | 4 |
| Comparative example 1 | 1100 | 980 | 5 |
| Comparative example 2 | 1090 | 990 | 6 |
| Comparative example 3 | 900 | 1000 | 5 |
Combining examples 3-4 and examples 5-6, and combining Table 2, it can be seen that the performance of examples 3-4 is superior to examples 5-6, demonstrating that ZrB 2 The particles are distributed in the grain boundary, the blocking effect of movement dislocation can be effectively increased by the finer particles, the strength and the elongation are improved, but the smaller particle size is easy to agglomerate in the grain boundary, and the influence is caused on the strength.
As can be seen by combining examples 3-4 and examples 7-8 with Table 2, examples 3-4 are superior to examples 7-8 in performance, zrO of fine particle size 2 The grain boundary is increased by the particles, and when an external force acts, the movement of dislocation is hindered to be increased, so that martensite is refined, thereby increasing the strength of the steel, but ZrO with smaller grain size 2 The particles are agglomerated at the grain boundary, so that the grains are excessively grown and cannot be refined, and the strength is reduced.
By combining examples 3-4 and examples 9-10 and table 2, it can be seen that the performance of examples 3-4 is better than that of examples 9-10, the heating temperature is low, the holding time is short, a uniform structure is difficult to obtain, the heating temperature should be kept above the recrystallization temperature of the blank to ensure austenitization of the blank, the holding time is prolonged, the crystal grain size is gradually increased, the effect of grain refinement cannot be achieved, and the performance is reduced.
Combining examples 3-4 and examples 11-12, and combining table 2, it can be seen that examples 3-4 are superior to examples 11-12 in performance, the martensite structure is difficult to form with an excessively low quenching rate, and the greater the cooling rate of the billet, the more easily the billet is hardened, resulting in increased brittleness.
Combining example 2 with comparative examples 1-3, and Table 2, it can be seen that examples 2-4 have better performance than comparative examples 1-3, with ZrB added 2 The particles act as age-hardening, zrO 2 The particles act to refine the grains, zrO 2 Can improve the effect of adding ZrB 2 The problem of increased toughness of the blank is caused, and the dual functions of grain refinement and dispersion strengthening enable the saddle plate to have ultrahigh strength.
The present embodiment is only for explaining the present application, and it is not limited to the present application, and those skilled in the art can make modifications of the present embodiment without inventive contribution as needed after reading the present specification, but all of them are protected by patent law within the scope of the claims of the present application.
Claims (8)
1. An ultra-high strength saddle plate, characterized in that: the saddle plate comprises the following raw materials in percentage by mass: 0.15 to 0.35 percent of C, 1.0 to 1.8 percent of Mn, less than or equal to 0.5 percent of Si, less than or equal to 0.005 percent of B, and the balance of Fe.
2. The ultra-high strength saddle plate as claimed in claim 1, wherein: the saddle plate comprises the following raw materials in percentage by mass: 0.2 to 0.28 percent of C, 1.3 to 1.5 percent of Mn, 0.3 percent of Si, 0.005 percent of B, 0.0017 to 0.02 percent of Zr, 0.17 to 0.2 percent of Al, and ZrB 2 0.004-0.006%，ZrO 2 0.001-0.003% of iron as the rest.
3. The ultra-high strength saddle plate as claimed in claim 2, wherein: the ZrB 2 The particle size is 20-35nm.
4. The ultra-high strength saddle plate as claimed in claim 2, wherein: the ZrO 2 Particle size of 40-50nm。
5. The method for manufacturing an ultra-high strength saddle plate according to any one of claims 1 to 4, wherein: the method comprises the following steps:
step one, smelting: uniformly stirring and smelting the raw materials in a vacuum induction electric furnace, and then casting into a steel plate;
step two, homogenization treatment: heating the steel plate to 1100-1150 ℃ in a heating furnace under the protection of inert gas, preserving heat for 1.5-2.5h, cooling to normal temperature in air, eliminating component segregation, rolling to the required material thickness, and cutting into part blanks;
step three, hot stamping and forming: and D, firstly, carrying out cold stamping on the blank obtained in the step two by using a pre-forming die, stamping the blank into the shape of the saddle plate part, then heating and preserving heat in the furnace, then quickly moving the saddle plate into the die for stamping, maintaining the pressure and quenching to obtain the saddle plate.
6. The method for manufacturing an ultra-high strength saddle plate according to claim 5, wherein: the heating temperature in the furnace in the third step is 900-950 ℃, and the heat preservation time is 3-10min.
7. The method for manufacturing an ultra-high strength saddle plate according to claim 5, wherein: the cooling rate of quenching in the third step is 20-30 ℃/s.
8. The method for manufacturing an ultra-high strength saddle plate according to claim 5, wherein: the thickness of the saddle plate is 1-4mm.
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