CN113684418A - High-hardenability hot-rolled hot-formed high-strength steel for tipping wagon carriage - Google Patents
High-hardenability hot-rolled hot-formed high-strength steel for tipping wagon carriage Download PDFInfo
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Abstract
本发明提供一种高淬透性的翻斗车车厢用热轧热成形高强钢，所述高强钢以重量百分比计，包括：0.20～0.40％的C、0.30～2.5％的Si、0.2～2.0％的Mn、0.01～2.0％的Cr、0.01～0.15％的Ti、0.0003～0.004％的B、0.01～0.4％的Al、0.01％以下的S、1.0％以下的Ni、0.5％以下的Nb、2.0％以下的V或Mo和余量Fe。本发明获取了高淬透性的热轧热成形高强钢，同时该钢种还具备优异的抗高温氧化性，能够应用于翻斗车车厢等超大尺寸热轧热成形汽车零部件，且适于推广。
The invention provides a hot-rolled and hot-formed high-strength steel for a dump truck carriage with high hardenability. The high-strength steel, in terms of weight percentage, comprises: 0.20-0.40% C, 0.30-2.5% Si, 0.2-2.0% Mn, 0.01-2.0% Cr, 0.01-0.15% Ti, 0.0003-0.004% B, 0.01-0.4% Al, 0.01% or less S, 1.0% or less Ni, 0.5% or less Nb, 2.0 % or less of V or Mo and the balance Fe. The invention obtains hot-rolled hot-formed high-strength steel with high hardenability, and at the same time, the steel also has excellent high-temperature oxidation resistance, can be applied to super-sized hot-rolled and hot-formed auto parts such as dump truck compartments, and is suitable for promotion .
Description
Technical Field
The invention relates to the technical field of steel materials, in particular to hot-rolled hot-formed high-strength steel with high hardenability for a tipping wagon carriage.
Background
Nowadays, the general trend of the development of automobile technology is safety, intelligence, energy conservation, environmental protection and the like, and especially the energy conservation and the environmental protection are more relevant to the sustainable development of human beings. With the increasing prominence of energy and environmental problems, the significance of automobile light weight becomes more important. The international aluminum association (IAI) indicates that fuel consumption can be reduced by 6% -8% for every 10% weight reduction of a car. Considering the huge automobile holding capacity in the world, reducing the mass of the automobile can effectively reduce the energy consumption and relieve the huge environmental pressure. According to statistics, the mass of the bodies of commercial vehicles such as dump trucks and freight trucks accounts for 16% -30% of the mass of the whole vehicle, and under the same condition, the smaller the mass of the whole vehicle is, the larger the load capacity is, and the higher the profit is. Under the current prerequisite that the commercial car strictly limits the overload, the lightweight of commercial car lifts the weight of foot, moreover under the situation of "carbon reaches the peak, carbon neutralizes" in the future, the lightweight of commercial car is inevitable.
Commercial vehicles started earlier in light weight abroad. The truck plan of 21 century was started in the United states in 2000, and the U.S. lightweight material technical special item of the United states truck was specially established. The project is set up to meet the requirements of 21 st century trucks on lightweight material technology, and aims to reduce the deadweight of trucks to reduce fuel consumption and maintain and enhance the functionality, durability, reliability, safety and purchaseability of crude oil of vehicles by adopting advanced design technology, material technology and manufacturing technology. The main application objects of the project are assembly parts such as a vehicle body, a chassis and a suspension. Compared with the similar type of vehicles abroad, the difference of the light weight level of commercial vehicles in China is obvious, for example, the preparation quality of a tractor VOLVO FE with the load of 40 tons is 7.69 tons, while the preparation quality of the similar type of vehicles in China is 9.95 tons, and the difference is over 20 percent.
In view of the current situation, the commercial vehicle is made of high-strength steel and aluminum alloy materials with the largest light-weight application potential, the high-strength steel can be used for a vehicle body, a vehicle frame, a carriage, a steel plate spring and the like, China successively experiences the application of steel types with different strength levels of 345MPa, 590MPa and 710MP, 700L steel is generally applied to the commercial vehicle frame due to the implementation of the overload regulations of the commercial vehicle in 2018, the obvious light-weight effect is achieved, but the carriage still takes Q345 as the main component, and the light-weight level still needs to be improved. The quenched hot formed steel 22MnB5 has tensile strength of more than 1500MPa, is widely applied to passenger vehicles, the amount of independent brands used by a single vehicle (white vehicle body) is nearly 10 percent, but the application of the quenched hot formed steel on commercial vehicles is less, if the hot formed steel is adopted to replace the existing commercial vehicle carriage steel plate, the weight of the single vehicle is reduced by more than 40 percent, the light weight effect is very obvious, and at present, the application of the hot rolled hot formed steel plate on commercial vehicles such as dump trucks and trucks has great market potential under the requirement of light weight rigidity.
However, at present, for example, large-size and thick hot-rolled hot-formed steel plates for dump truck carriages are not widely applied, and the reason is that a large problem needs to be solved in the stamping process: the conventional hot-rolled hot-formed steel sheet having a thickness of 3mm or more has insufficient hardenability, and it is difficult to obtain an ideal strength after hot forming.
Disclosure of Invention
In view of the above, it is necessary to provide a hot-rolled hot-formed high-strength steel for a dump truck body with high hardenability.
A high-hardenability hot-rolled hot-formed high-strength steel for a dumper carriage comprises, by weight, 0.20-0.40% of C, 0.30-2.5% of Si, 0.2-2.0% of Mn, 0.01-2.0% of Cr, 0.01-0.15% of Ti, 0.0003-0.004% of B, 0.01-0.4% of Al, 0.01% or less of S, 1.0% or less of Ni, 0.5% or less of Nb, 2.0% or less of V or Mo, and the balance Fe.
Further, the thickness of the high-strength steel is 2-8 mm.
Further, the preparation method of the high-strength steel comprises the working procedures of steel making, casting, hot rolling and acid pickling.
Further, the heating temperature of the casting blank is 1100-1300 ℃, and the heat preservation time is 0.5-10 h; the finishing temperature is 800-950 ℃; the coiling temperature is 550-700 ℃; the mass concentration of the pickling solution is 5-30%, and the temperature of the pickling solution is 50-100 ℃.
Further, the hot rolling hot forming process of the high-strength steel comprises the following steps: heating the steel plate for hot stamping forming to 880-950 ℃, and preserving heat for 3-10 min to completely austenitize the steel plate; after the steel plate is completely austenitized, the steel plate is sent into a die with a cooling system inside for stamping and forming; maintaining the pressure and rapidly cooling and quenching, wherein the cooling speed is controlled to be 15-200 ℃/s, so that the austenite is converted into martensite.
Further, the tensile strength of the high-strength steel after hot forming is 1400-2000 MPa.
Compared with the prior art, the invention has the advantages and beneficial effects that: the invention obtains the novel thicker hot-rolled hot-formed steel, and the hardenability of the steel is obviously improved; the hardenability of the material is improved by compounding elements such as Si, Cr, V or Mo and the like, the hot-rolled hot-formed steel with high hardenability is obtained, and the high-temperature oxidation resistance of the steel is improved by the Si, Cr and Al; the hot-rolled hot-formed steel with high hardenability and high-temperature oxidation resistance is obtained, and can be applied to oversized hot-rolled hot-formed automobile parts such as tipping wagon carriages.
Drawings
FIG. 1 is a graph of a simulated hardenability test experiment for an inventive steel and a comparative steel in one example of a range of low carbon steels;
FIG. 2 is a graph showing a simulation experiment of hardenability tests of an inventive example steel and a comparative example steel in the range of medium carbon steel in one example.
Detailed Description
In order that the invention may be more clearly understood, the following detailed description of the invention is given with reference to the accompanying drawings. It should be understood that the specific embodiments described herein are merely illustrative of the invention and are not intended to limit the invention.
In one embodiment, there is provided a hot rolled hot formed high strength steel for a high hardenability dump truck bed, the high strength steel comprising, in weight percent: 0.20 to 0.40% of C, 0.30 to 2.5% of Si, 0.2 to 2.0% of Mn, 0.01 to 2.0% of Cr, 0.01 to 0.15% of Ti, 0.0003 to 0.004% of B, 0.01 to 0.4% of Al, 0.01% or less of S, 1.0% or less of Ni, 0.5% or less of Nb, 2.0% or less of V or Mo, and the balance Fe.
In the present example, the hardenability of the material is improved by compounding elements such as Si, Cr, V, or Mo to obtain a hot-rolled hot-formed steel with high hardenability, and the high-temperature oxidation resistance of the steel is improved by Si, Cr, and Al; the hot-rolled hot-formed steel with high hardenability and high-temperature oxidation resistance is obtained, and can be applied to oversized hot-rolled hot-formed automobile parts such as tipping wagon carriages.
Wherein the thickness of the high-strength steel is 2 mm-8 mm.
The preparation method of the high-strength steel comprises the working procedures of steel making, casting, hot rolling and acid pickling.
In the working procedures, the heating temperature of the casting blank is 1100-1300 ℃, and the heat preservation time is 0.5-10 h; the finishing temperature is 800-950 ℃; the coiling temperature is 550-700 ℃; the mass concentration of the pickling solution is 5-30%, and the temperature of the pickling solution is 50-100 ℃.
The hot rolling hot forming process of the high-strength steel comprises the following steps: heating the steel plate for hot stamping forming to 880-950 ℃, and preserving heat for 3-10 min to completely austenitize the steel plate; after the steel plate is completely austenitized, the steel plate is sent into a die with a cooling system inside for stamping and forming; maintaining the pressure and rapidly cooling and quenching, wherein the cooling speed is controlled to be 15-200 ℃/s, so that the austenite is converted into martensite.
In particular, in practice, the structure obtained after cooling is mainly martensitic, allowing the presence of small amounts of ferrite, bainite or residual austenite without affecting the quality of the high-strength steel.
Wherein the tensile strength of the high-strength steel after hot forming is 1400-2000 MPa.
In one embodiment, the hardenability test and the quenched tensile strength test of the high-strength steel of the present invention are performed by a model experiment. Wherein, hardenability test simulation experiment specifically includes: the end-quench curves of each material in the composition table 1 were simulated and calculated using the Jominy Hardenability module in the JmatPro material performance simulation software. Wherein, JmatPro simulation conditions are set as follows:
the components: see composition table 1;
grain size: 7.4 ASTM;
quenching start temperature: 930 ℃;
length of metal bar: 10 cm;
the metal bar hardness test point taking distance is as follows: 0.5 cm.
Composition Table 1
Comparative example No.1, low carbon steel range, among others: 0.22C-0.22 Si;
inventive example No. 2: 0.24C-1.5Si-0.05Mo-0.02 Cr-0.02V;
inventive example No. 3: 0.22C-0.5Si-0.05Mo-1.5 Cr-0.02V;
inventive example No. 4: 0.22C-0.9Si-0.05Mo-0.4 Cr-0.02V;
comparative example No.5 of medium carbon steel range composition, among others: 0.35C-0.26Si
Inventive example No. 6: 0.38C-0.6Si-1.5Mo-0.02 Cr-0.02V;
inventive example No. 7: 0.38C-0.5Si-0.05Mo-0.02 Cr-0.4V;
inventive example No. 8: 0.38C-0.5Si-0.2Mo-0.3 Cr-0.2V.
In this example, the test results of the low carbon steel range composition are shown in FIG. 1, the hardenability of the steel in comparative example No.1 is the lowest, and the hardenability strengths of the steels in inventive examples No.2 to No.4 are all greater than that of comparative example No. 1; the test results of the range of the medium carbon steel are shown in FIG. 2, the hardenability of the steel in the comparative example No.5 is the lowest, and the hardenability strength of the steel in the invention examples No.6 to No.8 is greater than that of the comparative example No.5, so that the hardenability of the steel is improved and the stability of the strength of the steel is ensured.
Specifically, the simulation experiment of the quenched tensile strength of the hot-rolled hot-formed high-strength steel specifically comprises the following steps: the quenching performance of each material in the composition table 1 is simulated and calculated by adopting a Quench Properties module in JmatPro material performance simulation software. Wherein, JmatPro simulation conditions are set as follows:
the components: see composition table 1;
grain size: 7.4 ASTM;
quenching start temperature: 930 ℃;
cooling rate: 20 ℃/s;
end temperature of cooling: 20 deg.C
The test results are shown in Table 2, wherein the tensile strengths in the quenched state of the low-carbon steel range components No. 2-No. 4 and the medium-carbon steel range components No. 6-No. 8 are within 1400MPa-2000 MPa.
TABLE 2
In one embodiment, the hot rolled hot formed high strength steel of the present invention also has improved high temperature oxidation resistance, and the high temperature oxidation resistance of the hot rolled hot formed high strength steel is measured by: smelting and pouring by adopting a 50kg vacuum induction furnace, wherein the content of impurity elements is controlled as much as possible in the smelting process; heating the steel ingot to 1200 ℃, preserving heat for 2 hours, homogenizing, forging at the beginning forging temperature of 1150 ℃ and the end forging temperature of 850 ℃, and forging the ingot into a billet after multiple times of forging; keeping the temperature at 1200 ℃ for 1 hour for homogenizing treatment, and obtaining a hot rolled plate with the thickness of 3mm through multiple hot rolling, wherein the final rolling temperature is 800 ℃; and (3) pickling the hot rolled plate to remove surface oxide scale.
In order to better implement the invention, the composition table 3 shows the alloy compositions of some examples of the hot-rolled hot-formed high-strength steel of the invention and the alloy composition of the proportion 22MnB5, in the national standard GB/T13303-1991 steel oxidation resistance determination method, the determination method comprises a weight reduction method and a weight gain method, and in order to better show the high-temperature oxidation resistance of the hot-rolled hot-formed high-strength steel of the invention, the invention adopts a weight gain method for determination. In consideration of experimental errors caused by different measurement methods, the invention mainly adopts standard boron steel 22MnB5 as a comparative example for comparison.
Ingredient Table 3
| No. | C | Si | Mn | Al | Cr | B | Ti | Mo |
| 9 (comparison example) | 0.24 | 0.24 | 1.32 | 0.031 | 0.13 | 0.0021 | 0.031 | 0.0018 |
| 10 (comparison example) | 0.26 | 0.22 | 1.22 | 0.037 | 0.11 | 0.0022 | 0.021 | - |
| 11 (comparison example) | 0.21 | 0.26 | 1.25 | 0.030 | 0.13 | 0.0018 | 0.031 | - |
| 12 (inventive example) | 0.24 | 1.80 | 1.32 | 0.031 | 0.60 | 0.0021 | 0.031 | - |
| 13 (inventive example) | 0.37 | 1.80 | 1.32 | 0.300 | 0.25 | 0.0021 | 0.025 | - |
The experimental method comprises the following steps: a30 mm multiplied by 10mm multiplied by 3mm sample of the steel of the invention and 22MnB5 are respectively taken, firstly polished by 180#, 400#, 800#, 1500# and 2000# sandpaper, cleaned by alcohol and dried. The dimensions of the sample were measured with a vernier caliper, and the weight before oxidation was weighed with an electronic balance with an accuracy of 0.0001 g. The oxidation experiment is carried out in an air medium resistance furnace, the experiment temperature is 930 ℃, and the heat preservation time is 5 min. The sample after oxidation was weighed again, and the oxidation weight gain per unit area of the sample was calculated in combination with the size of the sample before oxidation.
In one embodiment, the hot-rolled hot-formed high-strength steel of the present invention has the following specific conditions for high temperature oxidation resistance test:
the oxidation at 930 ℃ for 5min is shown in Table 4: it can be seen that the oxidation weight gain, the unit area weight gain and the average unit area weight gain of invention examples 12 and 13 are significantly lower than those of comparative example 9 at 5 minutes of oxidation, i.e. the oxidation weight gain of the high-strength steel of the present invention is significantly lower than that of the standard boron steel, and therefore, the high-temperature oxidation resistance of the high-strength steel of the present invention is significant.
TABLE 4
In the present example, it can be seen from the comparison of the oxidation rates of the steels in the inventive example and the comparative example at 930 ℃ for 5min that the high-temperature oxidation resistance is significantly improved compared to the comparative example steel when Si, Cr and Al are compositely added at high contents.
The foregoing is a more detailed description of the present invention that is presented in conjunction with specific embodiments, and the practice of the invention is not to be considered limited to those descriptions. For those skilled in the art to which the invention pertains, several simple deductions or substitutions can be made without departing from the spirit of the invention, and all shall be considered as belonging to the protection scope of the invention.
Claims (6)
1. A high-hardenability hot-rolled hot-formed high-strength steel for a dump truck carriage, which is characterized by comprising the following components in percentage by weight: 0.20 to 0.40% of C, 0.30 to 2.5% of Si, 0.2 to 2.0% of Mn, 0.01 to 2.0% of Cr, 0.01 to 0.15% of Ti, 0.0003 to 0.004% of B, 0.01 to 0.4% of Al, 0.01% or less of S, 1.0% or less of Ni, 0.5% or less of Nb, 2.0% or less of V or Mo, and the balance Fe.
2. The hot rolled hot formed high strength steel for a dump truck bed with high hardenability according to claim 1, wherein the thickness of the high strength steel is 2mm to 8 mm.
3. The hot-rolled hot-formed high-strength steel for the dumper carriage with high hardenability according to claim 1, wherein the preparation method of the high-strength steel comprises the steps of steel making, casting, hot rolling and pickling.
4. The hot-rolled hot-formed high-strength steel for the dumper carriage with high hardenability according to claim 3, wherein the casting blank is heated at 1100-1300 ℃ for 0.5-10 h; the finishing temperature is 800-950 ℃; the coiling temperature is 550-700 ℃; the mass concentration of the pickling solution is 5-30%, and the temperature of the pickling solution is 50-100 ℃.
5. The hot-rolled hot-formed high-strength steel for the dump truck carriage with high hardenability according to claim 4, wherein the hot-rolled hot-formed process of the high-strength steel is as follows: heating the steel plate for hot stamping forming to 880-950 ℃, and preserving heat for 3-10 min to completely austenitize the steel plate; after the steel plate is completely austenitized, the steel plate is sent into a die with a cooling system inside for stamping and forming; maintaining the pressure and rapidly cooling and quenching, wherein the cooling speed is controlled to be 15-200 ℃/s, so that the austenite is converted into martensite.
6. The hot-rolled hot-formed high-strength steel for a dump truck bed with high hardenability according to claim 5, wherein the tensile strength of the high-strength steel after hot forming is 1400 to 2000 MPa.
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Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN113846272A (en) * | 2021-11-29 | 2021-12-28 | 东北大学 | Hot rolling preparation method of 1700MPa grade high Cr-Si thin-specification hot forming steel |
| CN114506256A (en) * | 2022-01-19 | 2022-05-17 | 吉林富锋汽车部件有限公司 | Lightweight self-discharging carriage |
| CN114990434A (en) * | 2022-05-18 | 2022-09-02 | 湖南华菱涟源钢铁有限公司 | Hot-formed steel material and method for producing same |
Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US20040149360A1 (en) * | 2002-12-05 | 2004-08-05 | Marc Robelet | Steel for mechanical construction, method of hot-shaping of a part from this steel, and part thus obtained |
| JP2005139485A (en) * | 2003-11-05 | 2005-06-02 | Nippon Steel Corp | Steel sheet for hot forming |
| CN105849296A (en) * | 2013-12-25 | 2016-08-10 | 株式会社神户制钢所 | Steel sheet for hot forming and method for manufacturing hot press formed steel member |
| CN106191678A (en) * | 2016-08-24 | 2016-12-07 | 武汉钢铁股份有限公司 | By the tensile strength of medium thin slab Direct Rolling >=1700MPa hot forming steel and production method |
| CN110257702A (en) * | 2019-06-24 | 2019-09-20 | 鞍钢股份有限公司 | Steel for hot stamping forming and hot forming method thereof |
-
2021
- 2021-08-11 CN CN202110918105.5A patent/CN113684418A/en active Pending
Patent Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US20040149360A1 (en) * | 2002-12-05 | 2004-08-05 | Marc Robelet | Steel for mechanical construction, method of hot-shaping of a part from this steel, and part thus obtained |
| JP2005139485A (en) * | 2003-11-05 | 2005-06-02 | Nippon Steel Corp | Steel sheet for hot forming |
| CN105849296A (en) * | 2013-12-25 | 2016-08-10 | 株式会社神户制钢所 | Steel sheet for hot forming and method for manufacturing hot press formed steel member |
| CN106191678A (en) * | 2016-08-24 | 2016-12-07 | 武汉钢铁股份有限公司 | By the tensile strength of medium thin slab Direct Rolling >=1700MPa hot forming steel and production method |
| CN110257702A (en) * | 2019-06-24 | 2019-09-20 | 鞍钢股份有限公司 | Steel for hot stamping forming and hot forming method thereof |
Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN113846272A (en) * | 2021-11-29 | 2021-12-28 | 东北大学 | Hot rolling preparation method of 1700MPa grade high Cr-Si thin-specification hot forming steel |
| CN113846272B (en) * | 2021-11-29 | 2022-03-01 | 东北大学 | Hot rolling preparation method of 1700MPa grade high Cr-Si thin-specification hot forming steel |
| CN114506256A (en) * | 2022-01-19 | 2022-05-17 | 吉林富锋汽车部件有限公司 | Lightweight self-discharging carriage |
| CN114990434A (en) * | 2022-05-18 | 2022-09-02 | 湖南华菱涟源钢铁有限公司 | Hot-formed steel material and method for producing same |
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