CN116219294A - Non-coating high-temperature oxidation resistant hot stamping forming steel added with Y element - Google Patents
Non-coating high-temperature oxidation resistant hot stamping forming steel added with Y element Download PDFInfo
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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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
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/18—Hardening; Quenching with or without subsequent tempering
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C33/00—Making ferrous alloys
- C22C33/04—Making ferrous alloys by melting
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/005—Ferrous alloys, e.g. steel alloys containing rare earths, i.e. Sc, Y, Lanthanides
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
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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
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/008—Martensite
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- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
- Y02P10/00—Technologies related to metal processing
- Y02P10/20—Recycling
Abstract
The present invention provides: the uncoated high-temperature oxidation resistant hot stamping forming steel added with the Y element is characterized by comprising the following alloy components in percentage by mass: c:0.2 to 0.4 percent, si:1.5 to 2.0 percent, mn:1.0 to 1.8 percent of Al:0.2 to 1.5 percent, ti:0.01 to 0.15 percent, B:0.0008 to 0.004 percent, Y:0.0002 to 0.01 percent, S: less than or equal to 0.01 percent, P: less than or equal to 0.01 percent, the balance being Fe and unavoidable impurities, wherein the content of Si+Al is 1.8 to 3.0 percent. The invention can inhibit the formation of loose oxide skin of hot stamping forming steel at high temperature, prevent the damage of a die and the generation of surface flaws of a product, and can obtain a paint film with the adhesive force of 0 level by directly coating in a shot blasting process, thereby reducing the alloy cost, reducing the process, reducing the production cost, improving the dimensional accuracy, obviously enhancing the toughness on the premise of ensuring the strength, and meeting the requirements of high-temperature oxidation resistance and mechanical property of the hot stamping steel.
Description
Technical Field
The invention is applied to the technical field of steel materials, and particularly relates to uncoated high-temperature oxidation resistant hot stamping forming steel added with Y element.
Background
The use of ultra-high strength steel is an important way for realizing the weight reduction of automobiles, but with the improvement of strength performance, the formability is obviously reduced, and the defects that cold forming is difficult to form, rebound is large, the size and shape stability of parts are poor and the like can be avoided by adopting a hot stamping mode for direct processing and forming, so that the hot stamping forming steel is mainly applied to the production of high-strength and difficult-to-form parts of automobiles. When the steel is heated, iron and alloy elements on the surface react with oxygen, carbon dioxide in an air medium, moisture in the air and the like to form an oxide film, namely an oxidation phenomenon. Loose oxide skin formed on the surface of the steel plate is easy to fall off in the forming process, so that the surface of the die is damaged, the service life of the die is reduced, and the surface of a hot formed part is damaged. In addition, the production of oxide scale on the surface of the steel plate makes the subsequent production process of the parts difficult, such as coating, welding and the like. At the same time, the thickening of the scale causes a decrease in thermal conductivity upon cooling, thereby affecting the performance of the hot-formed steel after quenching. In order to remove the scale, a shot blasting treatment is generally performed after the thermoforming. However, the shot blasting treatment is performed after the thermoforming, which not only increases the cost, but also deforms the part and reduces the precision of the part.
In order to solve the problem of high-temperature oxidation resistance of formed steel, two main solutions exist at present: firstly, a coating technology is adopted, and secondly, a non-coating technology is adopted. For the coating technology, the surface oxidation and decarbonization in the forming process can be prevented, the corrosion resistance after painting can be improved, the production procedures are increased, and the production cost is increased. For the non-coating technology, the high-temperature oxidation resistance of hot stamping forming steel is improved mainly by designing and regulating the alloy element and component proportion, but the technology is rarely researched at present and has a commercial application degree lower than that of the coating technology, and the non-coating technology at present mainly researches on a forming method, strength, oxidation degree and the like, but does not research on the paint film adhesive force of a steel plate. Chinese CN109972061a discloses an antioxidation ultra-high strength steel plate for hot stamping forming and a low temperature hot forming process, the patent technology increases the content of Mn to 6-8% by enlarging the addition of austenite region elements C and Mn, thereby significantly reducing austenitizing heating temperature, thereby reducing the high temperature oxidation degree of the steel plate, and simultaneously determining the appropriate addition amount of Cr, si, al alloy elements by calculation and reference tests, improving the high temperature oxidation resistance of the steel plate, and finally obtaining the thermal shock forming steel plate with yield strength not less than 1400MPa, tensile strength not less than 1700MPa, and elongation more than 10%. However, too high an Mn content is disadvantageous in terms of welding, adhesion, etc., and at the same time, the low hot forming temperature tends to lower the forming accuracy of the part. Patent CN111926248A discloses a hot stamping steel and a hot stamping process added with Ce alloy, which promote rapid formation of a Si-rich oxide layer by adding Ce (0.03-0.08%) element, thereby realizing improvement of a surface oxide layer structure, controlling the thickness of the oxide layer, and obtaining a thinner oxide layer. The patent technology has too high Ce element content, not only is easy to cause the blockage of a water gap of a crystallizer and can not realize continuous casting of steel, but also reduces the processability and improves the production cost.
It can be seen that although the prior art has a major breakthrough in both high temperature oxidation resistance and quasi-static mechanical properties, no technology has been available that combines the advantages of both. Because of the problem of oxidation of the surface of the coating, the adhesion force of the shot blasting coating is required to meet the requirements after thermoforming, and in order to solve the problems, the invention researches on the basis of the prior art, enhances the high-temperature oxidation resistance and toughness of hot stamping forming steel, and particularly ensures that the adhesion force of a paint film is qualified without shot blasting direct coating after thermoforming.
Disclosure of Invention
Aiming at the problems in the prior art, the invention provides the uncoated high-temperature oxidation resistant hot stamping forming steel added with the Y alloy, and aiming at the problems that the non-coating technology in the prior art is difficult to obtain good paint film adhesive force and the like, the invention can realize shot-free direct coating after hot stamping forming, reduces the production cost and meets the requirements of high-end markets.
The invention solves the technical problems by adopting the following technical scheme:
the technical scheme adopted by the invention is as follows: the uncoated high-temperature oxidation resistant hot stamping forming steel added with the Y element is characterized by comprising the following alloy components in percentage by mass: c:0.2 to 0.4 percent, si:1.5 to 2.0 percent, mn:1.0 to 1.8 percent of Al:0.2 to 1.5 percent, ti:0.01 to 0.15 percent, B:0.0008 to 0.004 percent, Y:0.0002 to 0.01 percent, S: less than or equal to 0.01 percent, P: less than or equal to 0.01 percent, the balance being Fe and unavoidable impurities, wherein the content of Si+Al is 1.8 to 3.0 percent.
Further, the hot stamping forming steel ladle contains 0.2-0.4% of C. C is an effective element for improving hardenability and enhancing strength of steel, and forms a martensitic structure when the mold is cooled, and 0.2% or more of C must be added to obtain a desired strength value; in addition, the content of C exceeds 0.4%, the strength after cooling the mold is too high to exceed the target range, and the ductility, toughness, weldability, delayed fracture (hydrogen embrittlement) and the like are reduced.
Further, the hot stamping steel ladle contains 1.5-2.0% of Si. Si affects the scale formation and its adhesion, an important element of the present invention. Si forms a layer of oxide scale on the surface during heating, can play a role in inhibiting oxidization, and obviously reduces the generation amount of loose oxide scale at high temperature; too high a Si content may decrease the toughness of the weld heat affected zone, deteriorate the weldability thereof, and Si may increase decarburization sensitivity of the steel sheet surface to decrease the overall strength of the part after hot forming.
Further, the hot stamping steel ladle contains 1.0-1.8% of Mn. Mn is an effective element for improving hardenability and strength of steel, and is required to be 1.0% or more in order to obtain a desired strength value at the time of mold cooling. However, if the content exceeds 1.8%, segregation becomes remarkable and uniformity of the material after hot rolling/die cooling is lowered. Preferably, the Mn content is 1.2 to 1.5%.
Further, the hot stamping forming steel contains 0.2-1.5% of Al. Al is an important element for affecting the scale formation and the adhesion thereof. Al is a deoxidizer, and in addition, the generation of loose oxide scale during hot forming can be significantly reduced, and the content must be controlled to 0.2% or more in order to obtain these effects. If the content exceeds 1.5%, the workability is lowered, and further, the toughness after hot forming is lowered. Preferably, the Al content is 0.4 to 0.8%.
Further, the hot stamping steel ladle contains 0.01-0.15% of Ti. Ti is a nitride forming element, and B preferentially forms a nitride, thereby preventing the generation of BN, and solid solution strengthening of B can be ensured. In order to obtain these effects, the content must be controlled to 0.01% or more. However, when the content exceeds 0.15%, the hot rolling load becomes large, so that hot rolling becomes very difficult, and the hardenability is lowered, and the toughness of the hot-formed part is further lowered. Preferably, the Ti content is 0.01 to 0.05%.
Further, the hot stamping forming steel ladle contains 0.0008-0.004% of B. B is an effective element for improving hardenability and toughness on the premise of a small amount of B. In order to obtain these effects, the B content must be controlled to 0.0008% or more. However, if B exceeds 0.004%, hot rolling load increases significantly, martensite and bainite are produced after hot rolling, and steel sheet breakage occurs.
Further, the hot press forming ladle contains 0.0002 to 0.01% of Y. Y affects the scale formation and its adhesion, and is one of the important elements of the present invention. Y suppresses the production of the scale and improves the adhesion of the scale, and the content thereof must be 0.0002% or more. If the content exceeds 0.01%, the above effects are saturated, and the desired results are not obtained, and the workability is lowered and the production cost is increased.
Further, the hot stamping steel also contains less than or equal to 1.0 percent of Nb and/or V and/or W and/or Ni and/or Mo. Nb, V, W, ni, mo is an effective element for strengthening steel and improving hardenability, and may be optionally added.
Further, the Mn content is 1.2 to 1.5%.
Further, the Ti content is 0.01 to 0.05%.
Further, the Al content is 0.4 to 0.8%.
Further, the mechanical properties of the hot stamping forming steel after being heated at 930 ℃ for 5min and rapidly subjected to pressure maintaining quenching are as follows: the yield strength is more than or equal to 1000MPa, the tensile strength is more than or equal to 1450MPa, the total elongation is more than or equal to 7.0%, and the strength-plastic product is more than or equal to 12.0GPa percent.
Further, the thickness of the hot stamping forming steel oxide layer is less than or equal to 4.0 mu m.
Further, the preparation process of the hot stamping forming steel comprises the procedures of steelmaking, continuous casting, hot rolling, pickling, cold rolling and annealing.
Further, the thermoforming process is as follows: heating the steel plate for hot stamping forming to 880-950 ℃, and preserving heat for 3-10 min to enable the steel plate to be completely austenitized; after the steel plate is completely austenitized, the steel plate is sent into a die with a cooling system inside for stamping forming; and (3) pressure maintaining, rapid cooling and quenching, wherein the cooling speed is controlled at 15-200 ℃/s, so that austenite is transformed into martensite. Preferably, the pressure maintaining is fast cooled and quenched, and the cooling speed is controlled to be 15-30 ℃/s, so that austenite is transformed into martensite.
In summary, compared with the prior art, the invention has the following beneficial effects:
1. in the invention, by adding Y, on one hand, oxide is formed on the surface of the steel plate and can be used as Al 2 O 3 、SiO 2 On the other hand, the atomic radius of Y is larger, and the lattice of Y is expanded after penetrating into the steel plate, so that the density of a short-circuit diffusion channel is increased, and the formation of hot forming steel oxide skin is promoted. At the same time, Y changes the lattice short-circuit diffusion speed of anions and cations so as to reverse the growth mechanism of the oxide scale, namely, the growth mainly based on cation diffusion is changed into the growth mainly based on anion diffusion, in particular, the alpha-Al is inhibited 2 O 3 Compared with Ce, the cracking can inhibit the growth rate of the oxide scale more effectively, and the thickness of the high-temperature oxide scale of the hot-forming steel can be reduced.
2. The oxides of Y, si and Al are formed at the interface of oxide scale and matrix, Y blocks the short-circuit channel for outward diffusion of cations in the oxide scale, so that the cations are diffused inwards along the grain boundary of the oxide scale, and form pinning effect along the grain boundary or deep into the matrix in the crystal boundary, the actual contact area of the oxide layer and the matrix metal is increased, the adhesion of the oxide scale and the matrix is increased, and Y and alpha-Al 2 O 3 The reaction generates dispersed YAG phase, so that the binding force of the oxide film is improved. While the oxide of Y acts as a vacancy trap, essentially interrupting the vacancy source creating cavities at the oxide skin/matrix interface and eliminating alpha-Al 2 O 3 The rolling of the layer increases the bonding area of the oxide scale and the steel plate matrix, so that the adhesiveness of the oxide scale is improved fundamentally. The segregation of microelements at the interface of oxide scale/matrix is caused by Al 2 O 3 The main reason for flaking is that Y can improve the purity of steel and reduce trace impurities at the interface; the adhesive force of the paint film is improved by combining the functions, and the paint can be directly coated after thermoforming.
3. According to the invention, the prior austenite and martensite lath bundles are effectively refined by adding the Y element, so that the strength and toughness of the steel plate can be improved.
4. According to the invention, the content of Al element is improved, and the hardenability of the material is effectively improved by matching with elements with good hardenability such as V, ni, nb, mo, B, and meanwhile, the requirements of the hardenability and high-temperature oxidation resistance of the hot stamping forming steel plate are met. The invention improves the toughness and high-temperature oxidation resistance of steel, can meet the requirements without performing shot blasting treatment after hot forming and directly coating the paint film, reduces the production cost and is suitable for industrial application.
Drawings
Fig. 1 is a graph showing the thickness of the surface oxide layers of example 1 and comparative example 2 in a non-coated high temperature oxidation resistant hot stamping steel added with Y element according to the present invention (a graph is a surface oxide layer graph of comparative example 2, b graph is a surface oxide layer graph of example 1).
Fig. 2 is a graph showing the adhesion test of the uncoated high temperature oxidation resistant hot stamping steel added with the Y element according to the present invention (a graph showing the adhesion test of comparative example 2, and b graph showing the adhesion test of example 1).
Detailed Description
The technical scheme of the invention is further described in detail below with reference to the attached drawings and specific embodiments. It is to be understood that the following examples are illustrative only and are not to be construed as limiting the scope of the invention. All techniques implemented based on the above description of the invention are intended to be included within the scope of the invention.
In a specific embodiment, there is provided a non-coated high temperature oxidation resistant hot stamping steel added with Y element, comprising the following alloy components in mass percent: c:0.2 to 0.4 percent, si:1.5 to 2.0 percent, mn:1.0 to 1.8 percent of Al:0.2 to 1.5 percent, ti:0.01 to 0.15 percent, B:0.0008 to 0.004 percent, Y:0.0002 to 0.01 percent, V:0.05-0.2%, nb: less than or equal to 0.2 percent, S: less than or equal to 0.01 percent, P: less than or equal to 0.01 percent, the balance being Fe and unavoidable impurities, and the content of Si+Al is 1.8 to 3.0 percent.
In a specific embodiment, there is provided a non-coated high temperature oxidation resistant hot stamping steel added with Y element, comprising the following alloy components in mass percent: c:0.2 to 0.4 percent, si:1.5 to 2.0 percent, mn:1.0 to 1.8 percent of Al:0.2 to 1.5 percent, ti:0.01 to 0.15 percent, B:0.0008 to 0.004 percent, Y:0.0002 to 0.01 percent, ni:0.05-0.2%, nb: less than or equal to 0.2 percent, S: less than or equal to 0.01 percent, P: less than or equal to 0.01 percent, the balance being Fe and unavoidable impurities, and the content of Si+Al is 1.8 to 3.0 percent.
In a specific embodiment, there is provided a non-coated high temperature oxidation resistant hot stamping steel added with Y element, comprising the following alloy components in mass percent: c:0.2 to 0.4 percent, si:1.5 to 2.0 percent, mn:1.0 to 1.8 percent of Al:0.4 to 0.8 percent, ti:0.01 to 0.15 percent, B:0.0008 to 0.004 percent, Y:0.0002 to 0.01 percent, V:0.05-0.2%, ni: less than or equal to 0.2 percent, S: less than or equal to 0.01 percent, P: less than or equal to 0.01 percent, the balance being Fe and unavoidable impurities, and the content of Si+Al is 1.8 to 3.0 percent.
In a specific embodiment, there is provided a non-coated high temperature oxidation resistant hot stamping steel added with Y element, comprising the following alloy components in mass percent: c:0.2 to 0.4 percent, si:1.5 to 2.0 percent, mn:1.0 to 1.8 percent of Al:0.4 to 0.8 percent, ti:0.01 to 0.15 percent, B:0.0008 to 0.004 percent, Y:0.0002 to 0.01 percent, W: less than or equal to 0.2 percent, S: less than or equal to 0.01 percent, P: less than or equal to 0.01 percent, the balance being Fe and unavoidable impurities, and the content of Si+Al is 1.8 to 3.0 percent.
In a specific embodiment, there is provided a non-coated high temperature oxidation resistant hot stamping steel added with Y element, comprising the following alloy components in mass percent: c:0.2 to 0.4 percent, si:1.5 to 2.0 percent, mn:1.0 to 1.8 percent of Al:0.4 to 0.8 percent, ti:0.01 to 0.15 percent, B:0.0008 to 0.004 percent, Y:0.0002 to 0.01 percent, V: less than or equal to 0.2 percent, S: less than or equal to 0.01 percent, P: less than or equal to 0.01 percent, the balance being Fe and unavoidable impurities, and the content of Si+Al is 1.8 to 3.0 percent.
The preparation process of the hot stamping forming steel plate comprises the procedures of steelmaking, continuous casting, hot rolling, pickling, cold rolling and annealing.
Smelting and casting by adopting a 50kg vacuum induction furnace, controlling the content of impurity elements as much as possible in the smelting process, heating the steel ingot to 1200 ℃, preserving heat for 2 hours, homogenizing, and carrying out forging at 1150 ℃ and 850 ℃ as final forging; forging the ingot into a billet after multiple times of forging. After the homogenization treatment at 1200 ℃ for 1 hour, hot rolling is carried out for a plurality of times to obtain a hot rolled plate, and the hot rolled plate is pickled and removedThe surface oxide skin is rolled in a cold rolling mill for multiple times until the thickness of the cold rolled sheet is 1.0-1.5 mm, and is annealed at 780-820 ℃ by adopting N 2 -H 2 Atmosphere protection, ensuring uniform annealing of the matrix and eliminating the banded structure.
The hot stamping forming process of the steel plate comprises the following steps: heating the steel plate for hot stamping forming to 880-950 ℃, and preserving heat for 3-10 min to enable the steel plate to be completely austenitized; after the steel plate is completely austenitized, the steel plate is sent into a die with a cooling system inside for stamping forming; and (3) pressure maintaining, rapid cooling and quenching, wherein the cooling speed is controlled at 15-30 ℃/s, so that austenite is converted into martensite, and the martensite is directly coated without shot blasting, and finally the hot formed part is obtained.
In order to better practice the present invention, the alloy compositions of some examples of the steel sheet of the present invention and the alloy compositions of the comparative examples (S:. Ltoreq.0.01%, P:. Ltoreq.0.01% in each of the examples of the present invention and the comparative examples) are shown in Table 1.
Table 1 chemical composition table (mass%) of each of examples and comparative examples
Comparative example 1 is a composition of a typical 22MnB5 steel on the market, and comparative example 2 is a composition of a steel to which no Y element is added. The oxidation resistance test and the main mechanical property test are carried out on each embodiment and the comparative example according to the national standard.
The hot rolling treatment was performed according to the following process in each of the examples and comparative examples in table 1, and then the detection was performed:
the oxidation resistance was measured according to the weight gain method of national standard GB/T13303-1991 method for measuring oxidation resistance of Steel, and the measurement results are shown in Table 2.
TABLE 2 weight gain per unit area of hot stamping steel (heating temperature: 930 ℃ C.; holding time: 5 min)
| Sample of | Before oxidation (g) | After oxidation (g) | Weight gain by oxidation (g) | Weight gain per unit area (g/m) 2 ) |
| Example 1 | 3.2318 | 3.2320 | 0.0002 | 0.36 |
| Example 2 | 3.1498 | 3.1500 | 0.0002 | 0.41 |
| Example 3 | 3.1669 | 3.1671 | 0.0002 | 0.39 |
| Example 4 | 3.1329 | 3.1332 | 0.0003 | 0.51 |
| Example 5 | 3.2063 | 3.2066 | 0.0003 | 0.49 |
| Comparative example 1 | 12.1334 | 12.1374 | 0.004 | 3.29 |
| Comparative example 2 | 6.8465 | 6.8486 | 0.0021 | 2.35 |
As can be seen from Table 2, the weight gain per unit area was reduced by more than 3 times as compared with the comparative example, and the weight gain per unit area was increased by 3.29g/m as compared with the 22MnB5 steel 2 Down to 0.36g/m 2 The addition of the Y element can improve the oxide layer structure of the material, thereby controlling the thickness of the oxide layer and greatly improving the high-temperature oxidation resistance of the steel plate. The thickness of the oxide layer after adding the Y element is less than or equal to 4 mu m, and can reach 2 mu m. Referring to FIG. 1, the thickness of the oxide layer of the steel sheet of comparative example 2, to which the Y element was not added, was about 9. Mu.m, and the thickness of the oxide layer was reduced by about 55%. In the invention, by adding Y, on one hand, oxide is formed on the surface of the steel plate and can be used as Al 2 O 3 、SiO 2 On the other hand, the atomic radius of Y is larger, and the lattice of Y is expanded after penetrating into the steel plate, so that the density of a short-circuit diffusion channel is increased, and the formation of hot forming steel oxide skin is promoted. At the same time, Y alters the lattice shortness of anions and cationsThe diffusion rate of the path is reversed, so that the growth mechanism of the oxide scale is changed from growth mainly based on cation diffusion to growth mainly based on anion diffusion, and particularly the alpha-Al is inhibited 2 O 3 Compared with Ce, the cracking can inhibit the growth rate of the oxide scale more effectively, and the thickness of the high-temperature oxide scale of the hot-forming steel can be reduced.
After the steel plates of each example and comparative example are processed according to the hot stamping forming process, the mechanical properties such as yield strength, tensile strength, elongation, strength-plastic product and the like are detected according to the national standard, and specific detection data are shown in table 3..
Table 3 mechanical properties vs. table
| Sample of | Yield strength (Mpa) | Tensile strength (Mpa) | Elongation (%) | Accumulation of strong plastic (Gpa ·%) |
| Example 1 | 1000 | 1560 | 8.5 | 13.26 |
| Example 2 | 1005 | 1560 | 8.3 | 12.95 |
| Example 3 | 1005 | 1550 | 8.2 | 12.71 |
| Example 4 | 1160 | 1750 | 7.6 | 13.30 |
| Example 5 | 1005 | 1560 | 8.2 | 12.79 |
| Comparative example 1 | 1055 | 1500 | 5.7 | 8.55 |
| Comparative example 2 | 1060 | 1560 | 7.0 | 10.92 |
As can be seen from Table 3, the steel plate has a yield strength of not less than 1000MPa, a tensile strength of not less than 1450MPa, a total elongation of not less than 7.0%, a strength-plastic product of not less than 12.0GPa and a strength-plastic product of stability after being heated at 930 ℃ for 5 min. By adding the Y element, the original austenite and the martensite plate bundles are thinned by enlarging an equiaxed crystal area and inhibiting the growth of recrystallized grains in the solidification process, and the strength and the toughness of the steel plate are improved.
Compared with the comparative example, the invention can improve the adhesiveness of oxide scale after adding the Y element, mainly because: the oxide of Y and Si, al forms at the interface of oxide scale-matrix, Y blocks the short-circuit channel of cation out-diffusion in oxide scale, so that oxygen ions diffuse inwards along the grain boundary of oxide scale, and form pinning effect along the grain boundary or in-crystal deep into matrix, increasing the actual contact area of oxide layer and matrix metal, increasing the adhesion of oxide scale and matrix, and Y and alpha-Al 2 O 3 The reaction generates dispersed YAG phase, so that the binding force of the oxide film is improved. While the oxide of Y acts as a vacancy trap, essentially interrupting the vacancy source creating cavities at the oxide skin/matrix interface and eliminating alpha-Al 2 O 3 The rolling of the layer increases the bonding area of the oxide scale and the steel plate matrix, so that the adhesiveness of the oxide scale is improved fundamentally. The segregation of microelements at the interface of oxide scale/matrix is caused by Al 2 O 3 The main reason for flaking is that Y can improve the purity of steel and reduce trace impurities at the interface; the adhesive force of the paint film is improved by combining the functions, and the paint can be directly coated after thermoforming.
The adhesion force tester is used for testing the adhesion force of the paint film of the steel, and the adhesion force of the paint film of each embodiment reaches 0 level, and referring to the attached figure 2, the distribution of the adhesion force of the paint film without adding the Y element is uneven, and the performance requirement of the product cannot be met.
The above description is merely a preferred embodiment of the present invention, and the scope of the present invention is not limited to the above examples. Any modification, equivalent replacement, improvement, etc. made by those skilled in the art without departing from the technical idea of the present invention should be included in the protection scope of the present invention.
Claims (8)
1. The uncoated high-temperature oxidation resistant hot stamping forming steel added with the Y element is characterized by comprising the following alloy components in percentage by mass: c:0.2 to 0.4 percent, si:1.5 to 2.0 percent, mn:1.0 to 1.8 percent of Al:0.2 to 1.5 percent, ti:0.01 to 0.15 percent, B:0.0008 to 0.004 percent, Y:0.0002 to 0.01 percent, S: less than or equal to 0.01 percent, P: less than or equal to 0.01 percent, the balance being Fe and unavoidable impurities, wherein the content of Si+Al is 1.8 to 3.0 percent.
2. The non-coating high temperature oxidation resistant hot stamping steel added with Y element as claimed in claim 1, characterized in that: the steel plate also contains less than or equal to 1.0 percent of Nb and/or V and/or W and/or Ni.
3. The non-coating high temperature oxidation resistant hot stamping steel added with Y element as claimed in claim 1, characterized in that: the Mn content is 1.2-1.5%.
4. The non-coating high temperature oxidation resistant hot stamping steel added with Y element as claimed in claim 1, characterized in that: the Ti content is 0.01-0.05%.
5. The non-coating high temperature oxidation resistant hot stamping steel added with Y element as claimed in claim 1, characterized in that: the content of Al is 0.4-0.8%.
6. A non-coated high temperature oxidation resistant hot stamping steel as claimed in any one of claims 1 to 5, wherein Y element is added, characterized in that: the yield strength of the steel plate after being heated at 930 ℃ for 5min and rapidly subjected to pressure maintaining quenching is more than or equal to 1000MPa, the tensile strength is more than or equal to 1450MPa, the total elongation is more than or equal to 7.0%, and the strength-plastic product is more than or equal to 12.0GPa percent.
7. The non-coating high temperature oxidation resistant hot stamping steel added with Y element as claimed in claim 1, characterized in that: the preparation process of the steel plate for hot stamping comprises the procedures of steelmaking, continuous casting, hot rolling, pickling, cold rolling and annealing.
8. The non-coating high temperature oxidation resistant hot stamping steel added with Y element as claimed in claim 7, characterized in that: the hot stamping forming process comprises the following steps: heating the steel plate for hot stamping forming to 880-950 ℃, and preserving heat for 3-10 min to enable the steel plate to be completely austenitized; after the steel plate is completely austenitized, the steel plate is sent into a die with a cooling system inside for stamping forming; and (3) pressure maintaining, rapid cooling and quenching, wherein the cooling speed is controlled at 15-200 ℃/s, so that austenite is converted into martensite, and the martensite is directly coated without shot blasting, and finally the hot formed part is obtained.
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