巴西专利BR112014000376B1 WEATHER RESISTANT STEEL SHEET AND ITS PRODUCTION METHOD

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专利摘要:
Patent summary: "Ultra-high strength steel plate, wear resistant, and production method thereof". The present invention relates to a wear resistant high strength steel plate having a brinell hardness of = hb420, comprising the following chemical components (in weight%), c: 0.205 - 0.25%, si: 0.20 - 1.00%, mn: 1.0 - 1.5%, p = 0.015%, s = 0.010%, al: 0.02 - 0.04%, ti: 0.01 - 0.03%, n = 0.006%, ca = 0.005%, and more than one element between cr = 0.70%, ni = 0.50%, mo = 0.30%, other components being iron and the inevitable impurities. The wear resistant steel plate production method comprises heating the continuous casting plate or ingot to a temperature of 1150 - 1250 ° C, and then rolling it in the austenite recrystallization zone, with the total reduction ratio not being less than 70% and the lamination termination temperature not less than 860 ° c; Cool the steel sheet rapidly at a speed of vmin ~ 50 ° c / s to the temperature range ms - 145 ~ ms - 185 ° c, then cool it in air to room temperature. The finished steel sheet with a thickness of 6 - 25 mm has a martensite and residual austenite structure (5 - 10%), a hardness of = hb420, a yield strength of = 1000 mpa, an elongation of = 18%, akv at -40 ° c from = 27 j and good cold bending property, especially has a remarkable tripping effect in use, substantially improving their wear resistance, thus meeting the high demand for wear resistant steel sheets in the relative industries.
公开号:BR112014000376B1
申请号:R112014000376-9
申请日:2012-05-25
公开日:2019-07-02
发明作者:Aiwen Zhang；Guodong Wang；Sihai Jiao
申请人:Baoshan Iron & Steel Co., Ltd.；
IPC主号:

专利说明:

Descriptive Report of the Invention Patent for WEAR RESISTANT STEEL PLATE AND ITS PRODUCTION METHOD.
Field of the Invention [001] The present invention relates to a high-strength steel sheet, in particular to a high-strength, wear-resistant steel sheet, with Brinell hardness of> HB420 and a method of producing it .
Background of the Invention [002] Wear is one of the main ways of damaging the material, which can cause surprisingly large economic losses. A large number of equipment used in industries, such as the metallurgical mine, agricultural machinery and the coal industry, fail mainly because of material wear and tear. According to statistics, in industrialized countries, economic losses caused by the wear and tear of mechanical equipment and components account for 4% of gross national production, in which abrasive wear accounts for 50% of total metallic wear. In China, steel consumed for material wear per year is up to more than one million tonnes, in which 60 - 80 tonnes of steel sheets are consumed per year only in intermediate grooves for transporting scratched sheets in coal mining .
[003] As an important type of steel, high-strength, low-wear-resistant alloy steel is widely applied to fields such as mining machinery, industrial machinery, agricultural machinery, and rail transport. With the rapid development of the Chinese industry, various mechanical equipment has become more complicated, bigger and lighter, which requires this type of steel used to produce this equipment, not only for greater hardness and strength, but also good toughness and performance
Petition 870190035569, of 15/04/2019, p. 7/34
2/19 conformation. In the last few decades, the research and application of high-strength and wear-resistant steels has developed very quickly. This type of steel is developed on the basis of weldable steel of high strength and low alloy, with good resistance to wear and its useful life being many times longer than that of steel sheet of traditional structure; its production process is simple, which usually includes quick cooling and quenching, directly after lamination, or controlled lamination and controlled cooling to reinforce.
[004] Now, in the field of high strength and wear resistant, there have been many relative patents and patent applications in China and other countries. Regarding high-strength, low-carbon (0.205 - 0.25%) wear-resistant steel, it is necessary to add Nb, V or B in the patents JP1255622A, JP2002020837A, CN101469390, CN101186960A and CN101775545A, and many expensive connecting elements in JP2002020837A, JP2002194499A, CN1208776A, CN101469390A, CN101186960A and
CN101775545A. As for the processes, in many of these patents, rapid cooling (DQ or heating outside the line and rapid cooling) + tempering outside the line is adopted, with which the low temperature impact value at -40 ° C of the plate Finished steel is not high, that is, mainly between 17 - 50 J, which cannot reach user demand.
[005] A wear-resistant Hardox400 steel plate (4 32 mm) (C <0.18, Si <0.70, Mn <1.6, P <0.025, S <0.010, Ni <0.25, Cr <1.0, Mo <0.25, B <0.004) produced by Sweden SSAB, contains a low content of expensive bonding elements, with a hardness of between HBW370 - 430, and good wear resistance. The 20 mm thick steel plate typically has a yield limit of 1000 MPa, A50 of 16%, and longitudinal Akv at -40 ° C of 45J. Although your duPetition 870190035569, of 15/04/2019, p. 8/34
3/19 pray, resistance and wear resistance are high, both their standard values and physical impact are not high and do not have the TRIP effect (self-hardening) in use.
[006] Currently, it is necessary to provide a medium strength steel plate with high resistance and wear resistance with TRIP effect. SUMMARY OF THE INVENTION [007] The purpose of the present invention is to provide a high-strength, wear-resistant medium steel plate with Brinell hardness of> HB420, particularly to provide such a plate having a thickness of 6 - 25 mm.
[008] To achieve the aforementioned objective, the medium steel sheet of the present invention contains the following chemical components, in% and weight, C: 0.205 - 0.25%, Si: 0.20 - 1.00%, Mn : 1.0 - 1.5%, P <0.015%, S <0.010%, Al: 0.02 - 0.04%, Ti: 0.01 0.03%, N <0.006%, Ca <0.005% , and more than one element between Cr <
0.70%, Ni <0.50%, Mo <0.30%, the balance being iron and the inevitable impurities.
[009] The structure of the steel sheet consists of martensite and residual austenite, in which residual austenite accounts for 5 - 10%. [0010] Another objective of the present invention is to provide a method for producing the wear-resistant high-strength steel plate with Brinell hardness of> HB420, which is comprised of:
(1) after the vacuum degassing treatment, continuous casting or conventional casting of the molten steel is performed, and if the molten steel is conventionally cast, laminate it in an ingot;
(2) heat the continuous caster plate or ingot to a temperature of 1150 - 1250 ° C, then laminate it in one pass or in multiple passes in the austenite recrystallization zone, with the total reduction ratio being no less than 70% and the temperature of
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4/19 end of lamination being not less than 860 ° C;
(3) cool the water quickly to the laminated steel sheet at a speed of Vmin ~ 50 ° C / s to the temperature range Ms - 145 ~ Ms - 185 ° C, then cool it in air to room temperature, in whereas the hardening index P is calculated according to the expression (i) [0011] P = 2.7C + 0.4Si + Mn + 0.45Ni + 0.8Cr + 0.45Cu + 2Mo, the critical cooling speed Vmin for obtaining martensite is calculated according to the expression (ii) lgVmin = 2.94-0.75P, and the starting temperature of the conformation of the martensite Ms is calculated according to the expression (iii) Ms = 561-474C-33Mn- 17Cr-17Ni-21Mo.
[0012] The inventor found that, in the wear-resistant steel plate structure, when the residual austenite content accounts for a certain value (for example,> 5%), the steel layer can have an apparent TRIP effect, which it can substantially improve the hardness and wear resistance of the surface. TRIP is short for TRansformation Induced by Plasticity and the TRIP effect means that when the steel sheet is perforated or subjected to an impact load, the residual austenite there can change from phase to martensite, making the part deformed quickly harden in order to resist another deformation, while simultaneously transferring the deformed part to the adjacent position, thus obtaining a very high elongation, that is, plasticity. As for the wear-resistant steel plate, when it is impacted or deformed by friction by other materials, the residual austenite in the deformed part is converted into martensite, with the consumption of energy brought about by the impact of the material or by the friction deformation, which reduces abrasion loss and improves its wear resistance. The structures of conventional wear-resistant plates are mainly martensite or bainite and few residual austenites and, because of this, the amount of residual austenite is small. Petition 870190035569, of 15/04/2019, p. 10/34
5/19 na. The TRIP effect may not occur, for example, on the wear-resistant steel sheet Hardox400 produced by Sweden SSAB.
[0013] The present invention loves an adequate carbon content, low-cost bonding elements Si and Mn, and few expensive bonding elements, Cr, Ni and Mo, without Cu, Nb, V, B, etc., which reduces the cost of connecting the steel plate, that is, having notable advantages over the cost of the connection. As for lamination, controlled lamination in the non-recrystallization zone is unnecessary, reducing the loads of the laminators, and it is only necessary to quickly cool the water to the laminated steel sheet at a speed of Vmin ~ 50 ° C / s up to the temperature range Ms -145 ~ Ms - 185 ° C, and then cool it in air to room temperature. The steel plate structure with a thickness of 6 - 25 mm is martensite and residual austenite (5-10%), which has a hardness of> HB420, a yield limit of> 1000 MPa, an elongation of> 18%, Akv at -40 ° C> 27 J and good cold bending property and, in particular, has a remarkable TRIP effect in use, substantially improving surface hardness and wear resistance, thus achieving high demand for steel sheets wear resistant in relative industries.
Brief Description of the Drawings [0014] Fig.1 is the schematic view of the process flow of the finished martensite and the residual austenite obtained by the line cooling and air cooling according to the present invention, where Temp indicates temperature; T.A indicates room temperature; Bs indicates the temperature at which bainite conversion starts; Bf indicates the finishing temperature of the bainite conversion; Ms indicates the conversion temperature of the martensite; and B-UTC indicates ultra-fast cooling.
[0015] Fig.2 is a photo of a typical metallographic structure of the ultra-high strength steel plate with a thickness of 15 mm of modality 3 according to the present invention.
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6/19 [0016] Fig.3 is a schematic view of comparison in the tendency of change in hardness between the present invention and conventional steel when delivered and used.
DETAILED DESCRIPTION OF THE INVENTION [0017] Hereinafter the present invention will be described in detail with respect to the modalities.
[0018] In the present invention, unless otherwise specified, the content here always indicates weight percent.
[0019] To achieve the goal of providing a high strength and wear resistant medium steel plate with Brinell hardness of> HB420, particularly to provide a medium steel plate having a thickness of 6 - 25 mm, the present invention chooses basic components and controls their contents as follows, and the reasons are also described.
[0020] Carbon: carbon is the key element to guarantee the strength of the steel plate. To obtain steel sheets consisting mainly of martensite and residual austenite, carbon is the most important element, which can significantly improve the hardening capacity of steel sheets. Due to the high solubility of carbon in austenite, it can maintain the high stability of austenite, and decrease the steel's Ms point, which is good for obtaining a certain amount of residual austenite. At the same time, increasing the carbon content can cause strength and hardness to improve and plasticity to decline, so if the steel sheet needs high strength and toughness and residual 5 - 10% austenite, p carbon content should not be too much low. Considering the above factors comprehensively, for a hardness of HB420 in the present invention, a carbon content of 0.205 - 0.25% is suitable. Preferably, the carbon content is 0.205 - 0.245%.
[0021] Silicon: the addition of silicon to steel can improve the purity and
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7/19 the deoxygenation of steel. The silicon in steel contributes to the reinforcement of the solid solution, and due to the high solubility of silicon in austenite, with increased silicon it is good for promoting the strength and hardness of steel and improving the stability of austenite especially when the steel plate, after being quickly cooled directly on the line and reheated on the line to the temperature range of the bainite, it is tempered, it can cause the carbides in the martensite to precipitate and the carbon to disperse in the residual austenite, so that the carbon content in the residual austenite increases, and austenite is stabilized without conversion until room temperature and that the steel sheet at room temperature obtains a structure composed of tempered martensite and residual austenite, which in use has the TRIP effect, thus improving wear resistance. But excess silicon can cause the steel's toughness to decline, and when the steel sheet with excess silicon is heated, its oxide film can become highly viscose, and it is difficult to remove the scale after the steel sheet leaves the oven, thus resulting in a portion of red oxide films on the laminated steel sheet, that is, the surface quality is poor; in addition, excessive silicon can also be detrimental to the weldability of the steel plate. In consideration of all the above factors, the silicon content in the present invention is 0.20 - 1.00%. Preferably, the silicon content is 0.20 - 0.99%.
[0022] Manganese: Manganese is used to stabilize austenite structures, and this capacity is second only to the nickel bonding element. It is an inexpensive element to stabilize austenite structures and strengthen the bond. At the same time, manganese can improve the steel's hardening capacity and decrease the critical cooling rate of martensite formation. However, manganese has a high tendency to segregate, so its content should not be too high, usually no more than 2.0% in low carbon microalloyed steel.
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The amount of manganese added in the present invention must be controlled within 1.0 - 1.5%. In addition, manganese together with aluminum in steel contributes to deoxygenation. Preferably, the manganese content is 1.11 - 1.45%.
[0023] Sulfur and Phosphorus: in steel, sulfur, manganese and the like are composed in a plastic inclusion, manganese sulphide, which is especially harmful for cross ductility and for its toughness, so it should be as low as possible. The phosphorus element in steel is also one of the harmful elements, which seriously impairs the ductility and toughness of steel sheets. In the present invention, both sulfur and phosphorus are inevitable impurities that should be as little as possible. In view of the current steel production conditions, the present invention requires that P be <0.015%, S be <0.010%. Preferably, the P content is <0.009%, and the S content is <0.004%.
[0024] Aluminum: in the present invention, aluminum acts as a strong deoxidation element. To ensure the oxygen content as low as possible, the aluminum content must be controlled to be between 0.02 - 0.04%. After deoxidation, the remaining aluminum is combined with nitrogen in the steel to form AlN precipitation which can improve strength and, during heat treatment, refine austenite grains. Preferably, the aluminum content 0.021 0.039%.
[0025] Titanium: Titanium is a strong carbide-forming element. The addition of Ti to the steel is good for stabilizing the N, and the TiN formed can also form the austenitic grains of the ingot, when heated, not making it too brutish, thus refining the original austenitic grains. In steel, titanium can be composed of carbon and sulfur respectively to form TiC, TiS, Ti4C2S2, and the like, which exist in CE form inclusions and second phase particles. CurrentPetition 870190035569, of 15/04/2019, p. 14/34
9/19, treatment with traces of titanium has been a conventional process for most high-strength and low-carbon steels. In the present invention, the titanium content is controlled to be between 0.01 - 0.03%. Preferably, the titanium content is 0.013 0.022%.
[0026] Chromium: chromium promotes the hardening capacity and resistance to tempering of steel. Chromium has good solubility in austenite and can stabilize austenite. After rapid cooling, most of it dissolves in the martensite and subsequently, in the tempering process, it precipitates carbides, such as Cr23C7, Cr C3, which improves the strength and hardness of the steel. To maintain the strength level of steel, chromium can partially replace manganese and weaken its tendency to segregate. Consequently, in the present invention, no more than 0.70% chromium can be added. Preferably, the chromium content is 0.35 - 0.65%.
[0027] Nickel: nickel is the element used to stabilize austenite with no noticeable effect on improving strength. The addition of nickel to steel, particularly in quenched and quenched steel, can substantially promote toughness, particularly its low temperature toughness, but it is an expensive bonding element, so the present invention can add no more than 0.50 % nickel. Preferably, the nickel content is 0.16 - 0.40%.
[0028] Molybdenum: molybdenum can significantly refine grains, and improve the strength and toughness of steel. It reduces the embrittlement in steel tempering while precipitating very fine carbides during tempering, which can remarkably strengthen its matrix. Since molybdenum is a type of strategic linker that is very expensive, in the present invention no more than 0.30% molybdenum is added. Preferably the molybdenum content is 0.18 0.24%.
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10/19 [0029] Calcium: the addition of calcium to the steel is mainly to change the shape of the sulfides, thus improving the transversal performance of the steel. For steel with a very low sulfur content, calcium treatment may not be necessary. The calcium content is less than or equal to 0.005%. Preferably, the calcium content is 0.001 - 0.003%. [0030] Nitrogen: the present invention does not contain the microalloyed elements Nb and V, and the forms of reinforcement are reinforcement of the phase change and reinforcement by tempered carbide precipitation. A nitrogen content less than or equal to 60ppm can stabilize 0.01 - 0.03% of titanium and form TiN, which can guarantee that when the matrix is heated, the austenite grains there do not become too brutish. In the present invention, the nitrogen content is <0.006%. Preferably, the nitrogen content is 0.0033 - 0.004%.
[0031] In the present invention, the addition of elements such as carbon, nickel that can improve the stability of austenite, can increase the residual austenite content in the cooled steel, which is good for the steel to obtain the TRIP effect. In addition, the process of controlling the temperature of the final cooling and without quenching can also increase the residual austenite content.
[0032] The following processes have an effect on the products of the present invention:
application of the Bessemer process and vacuum treatment. Its purpose is to ensure that molten steel contains basic components, to remove harmful gases such as oxygen, hydrogen, to add necessary binding elements such as manganese, titanium, and to adjust them.
[0033] Continuous casting or conventional casting: its objective is to ensure that the matrix has homogeneous internal components and good surface quality, in which static ingots formed by conventional casting will need to be laminated in lingoPetição 870190035569, of 15/04/2019, p. 16/34
11/19 tes;
heating and rolling: heat the continuous casting plate or ingot to a temperature of 1150 - 1250 ° C to obtain, on the one hand, the uniform austenite structure and, on the other hand, partially dissolve the compounds of the connecting elements such as titanium, chrome. Roll it in one pass or more than three passes in the austenite recrystallization temperature range on the steel plate, with the total reduction ratio being no less than 70%, and the rolling end temperature being no less than 860 ° C (preferably 860 - 890 ° C);
rapid cooling: according to expression (i), calculate the hardening index P and according to expression (ii), calculate the critical cooling speed Vmin to obtain martensite and then, according to expression (iii), calculate the start temperature of the martensite formation Ms. Cool the water quickly to the rolled steel sheet at a speed of Vmin ~ 50 ° C / s (preferably 16 - 50 ° C / s) up to the temperature range of Ms-145 ~ Ms-185 ° C, then cool it in air to room temperature. During rapid cooling, most of the connecting elements are dissolved in the martensite, and due to the control of the final cooling temperature, the structure maintains a certain amount of residual austenite, for example, 5 - 10%. Residual austenite guarantees the steel plate in use to obtain the TRIP effect.
[0034] In the present invention, using the appropriate component design, controlled lamination, rapid cooling, temperature control process of the final cooling, the steel sheet has fine grains ,. Phase change and increased precipitation. Fig.1 is a schematic view of the process for controlling the steel sheet structure. The finished structure of the steel plate has martensite and residual austenite, for example, Fig. 2 shows a typical structure of the
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12/19 15 mm thick steel plate. The finished steel sheet with a thickness of 6 - 25 mm has a hardness of> HB420, a yield limit of> 1000 MPa, an elongation of> 18%, Akv at 40 ° C of> 27 J and a good property of Cold bending, especially has a notable TRIP effect in use, substantially improving its surface resistance, hardness and wear resistance, thus reaching the high demand for wear resistant steel sheets in the relative industries. Fig.3 is a schematic view of the hardening effect of the steel plate surface in use.
[0035] The high-strength, wear-resistant medium steel plate, made using the component design mentioned above and the process control method, is used to produce members in various industries. Because of this, the steel sheet has a remarkable TRIP effect, it has low hardness when delivered, which is convenient for users to machine to the final shape, and when in use, its hardness can be substantially improved, with its wear resistance greatly improving.
Modalities [0036] Hereinafter, the present invention will be described in detail in relation to the modalities. These modalities are only the optimal modes of the present invention, but they do not limit its scope. Table 1 shows the chemical components, equivalent carbons, and minimum cooling rate of the steel sheets of the modalities, Table 2 shows the process parameters of the same, and Table 43 shows the properties of the finished steel sheet obtained by the modalities.
Mode 1 [0037] The molten steel according to the compatibility ratio in Table 1, after vacuum degassing, is cast continuously or conventionally, obtaining a 80 mm thick plate. The plate is heated to 1200 ° C, and laminated in multiple
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13/19 passes in the austenite recrystallization temperature range on a steel plate with a thickness of 5 mm, where the total reduction rate is 94%, the finishing temperature of the lamination is 890 ° C; it is then cooled to 250 ° C at a speed of 50 ° C / s, after which the steel sheet is air-cooled to room temperature.
[0038] Process flows for modes 2 - 6 are similar to those for mode 1, and their detailed components and processing parameters are shown in Table 1 and Table 2. The properties of the steel sheet in the modes are shown in Table 3.
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Table 1 - Chemical Components, Ceq (% by weight) and Critical Cooling Cup Vmin (° C / s) to obtain Martensite in Modes 1 - 6 of the present invention
Fashion-lities Ç Si Mn P s AAl Ni Cr Mo You Here N Ceq * Vmin 1 0.205 0.35 1.35 0.007 0.003 0.025 0.20 0.45 0.18 0.015 0.0038 0.57 6 2 0.214 0.45 1.45 0.008 0.003 0.021 0.16 0.35 0.22 0.022 0.004 0.58 5 3 0.228 0.20 1.11 0.007 0.003 0.039 0.23 0.55 0.21 0.015 0.0035 0.58 7 4 0.20 0.99 1.38 0.007 0.003 0.026 0.20 0.47 0.20 0.018 0.0036 0.58 5 5 0.232 0.25 1.20 0.008 0.003 0.036 0.38 0.60 0.19 0.014 0.002 0.0033 0.62 5 6 0.245 0.30 1.19 0.008 0.003 0.029 0.40 0.65 0.24 0.013 0.002 0.0039 0.64 3
* Ceq = C + Mn / 6 + (Cr + Mo + V) / 5 + (Ni + Cu) / 14
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Table 2 - Process Parameters Relating to Heating, Rolling and Cooling and Steel Sheet Thickness in Modes 1 - 6 of the Present Invention
Modali-dades Temperatureheatedment/ ° C Temperatureendlaminationnation/ ° C Rate ofreduction/% Speedcool-ment/ ° C / s Final temperaturecooling/ ° C Thickness ofplate/ mm 1 1150 890 94 50 250 6 2 1150 870 88 36 255 10 3 1250 860 80 25 280 15 4 1150 860 80 22 270 15 5 1200 860 75 22 255 20 6 1150 860 70 18 235 25
Test 1: Mechanical Properties of Steel Sheet [0039] According to GB / T228-2002 Metallic materials — the tensile test at room temperature and GB 2106-1980 Metallic materials — Charpy impact test with V-notch, the properties Mechanical, that is, the yield strength, tensile strength, elongation, and impact toughness at -40 ° C, etc., are measured, with the result shown in Table 3.
Test 2: Hardness [0040] According to test GB / T 231.1-2009, Brinell hardness of modalities 1 - 6 in the present invention is measured, with the result shown in Table 3.
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Table 3 - Mechanical Properties of Steel Sheets from
Present invention
Mo-dali-gives-des Du-pray/ HB yieldedmentof re-system-co/ MPa Resis-strengthtraction/ MPa Alon-ga-mentA50 /% Tenacity ofimpactat -40 ° CAkv / J Cold cross-folding d = 2a, 180 ⁰ Es-trutu-ras 1 420 1035 1345 19.3 31 PASS M + Air 2 425 1045 1360 19 42 PASS M + Air 3 430 1055 1385 20 55 PASS M + Air 4 440 1065 1410 20 63 PASS M + Air 5 455 1110 1455 19 58 PASS M + Air 6 460 1150 1480 18.5 61 PASS M + Air
M: martensite
Air: residual austenite, 5-10% Test 3:
[0041] The steel metallographic structures of the Modalities in the present invention are measured by an optical microscope, with the result shown in Table 3. The steel plate metallographic structures of all modalities are martensite and 5 - 10% residual austenite.
[0042] Fig.2 is a photo of a typical metallographic structure of the ultra-high strength steel plate with a thickness of 15 mm of modality 3 in the present invention. Metallographic structures similar to that of Fig. 2 can be obtained from other modalities.
Test 4: Cross Cold Bending Properties [0043] According to GB / T 232-2010 Metallic materials wingspan test, steel sheets in modalities 1 - 6 folded
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17/19 across the cold to d = 2a, 180 °, with the result shown in Table 3.
Test 5: Welding Performance Test [0044] According to GB4675.1-84 Inclined Y-notch welding crack test, the welding performance of modality 6 in the present invention is estimated , with the result shown in Table 4. It can be seen from Table 4 that the steel plate of modality 6 does not fracture after being welded under the preheat temperature conditions of 75 ° C, which indicates that the steel plate of this invention is of excellent welding performance.
Table 4 - Result of the Small Grinding Test of Steel of Type 6 of the Present Invention
No. Rate offracture ofsurface/% Rate offracture ofroot/% Rate offracture ofsection/% Preheat temperature Tem-ruraenvironmentyou Moisturerelative 1 0 0 0 2 0 0 0 3 0 0 0 75 ° C 30 ° C 60% 4 0 0 0 5 0 0 0 [0045] In other modalities, the same results can be
obtained, that is, the surface fracture rate (%), and the section fracture rate (%) are all 0.
Test 6: Wear Resistance Test [0046] The wear resistance test is conducted on an MG2000 grain abrasion testing machine. A cylindrical sample with a diameter of 5.0 mm and a length of 20 mm is placed on a friction disk and rotates circularly. A # 10 abrasive paper is attached to the friction disc, and a pin under a load pressure of 30 N is tested for friction consumption. The sample has a repeat speed 870190035569, from 15/04/2019, p. 23/34
18/19 lative 0.8 m / s, a friction distance of 200 mm, a test temperature of T = 25 ° C. A TG328A photoelectric analytical balance is used for weighing, and the loss in pin weight before and after the test indicates wear loss.
[0047] Comparative tests on wear resistance are carried out between modality 2 of the present invention and the HARDOX400 wear-resistant steel produced by Sweden SSAB. Because there is a difference in hardness between modality 2 and the comparative material, taking modality 2 as a reference, the hardness and wear loss of the HARDOX400 wear-resistant steel plate (with HB405 hardness) is converted, and indicated as absolute wear loss, hardness difference and wear loss difference, which are shown in Table 5. It is known from Table 5 that compared to produced by Sweden SSAB, the ultra-high wear resistant steel plate of the present invention has a great extent of improvement (about 30%) in wear resistance,
Table 5 - Comparative Results in Resistance to
Wear between Mode 2 and HARDOX400 Wear Resistant Steel
Steel Grade(toughness) Temperaturetest Conditions ofwear test Loss bywear(mg) Differenceof hardness% Differenceof lossby wear /% Modality2 (HB425) Room temperature Abrasive paper100 #, charge30N, speedrotation0.8m / s, distancefriction 200 m 24 0 0 HAR-DOX400 (HB405) 25 ° C 34 -5 +42
[0048] In other modalities, the wear resistance of the acquired steel sheet is also better than that of the HARPetição steel sheet 870190035569, of 15/04/2019, p. 24/34
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DOX400 (its hardness is HB400) produced by Sweden SSAB.
[0049] It can be seen from the above modalities, by using the component design mentioned above and suitable process parameters, the tempered steel sheet with a thickness of 6 - 25 mm has a hardness of> HB420, a yield limit of> 1000 MPa, an elongation of A50> 18%, Akv at -40 ° C> 27 J and good cold bending property, and its structures have martensite and residual austenite (5 - 10%). It has good welding performance and wear resistance which, compared to imported HB400 wear resistant steel plate, improves by about 30%. Especially, the steel plate has low hardness when delivered, which is convenient for users to machine to the desired shape, and when in use, due to the fact that the steel plate has a remarkable TRIP effect, its surface resistance, its hardness and wear resistance can be substantially improved, thus reaching the high demand for wear resistant steel sheet in the relative industries.

权利要求:
Claims (19)
[1]
claims
1. Wear-resistant steel plate, characterized by the fact that they consist of the following chemical compositions, by weight:
C: from 0.20 to 0.25%,
Si: from 0.20 to 1.00%,
Mn: from 1.0 to 1.5%,
P <0.015%,
S <0.010%,
Al: from 0.02 to 0.04%,
Ti: from 0.01 to 0.03%,
N <0.006%,
Ca <0.005%, more than one between Cr <0.70%,
Ni <0.50%, and
Mo <0.30%, and the balance being iron and the inevitable impurities, and the wear resistant steel plate structures are tempered martensite and 5 to 10% residual austenites.
[2]
2. Wear-resistant steel plate, according to claim 1, characterized by the fact that the carbon equivalent is 0.57 to 0.64.
[3]
3. Wear-resistant steel plate according to claim 1 or 2, characterized by the fact that C is 0.205 to 0.245% by weight.
[4]
Wear-resistant steel plate according to any one of claims 1 to 3, characterized by the fact that Si is 0.20 to 0.99% by weight.
[5]
Wear-resistant steel plate according to any one of claims 1 to 4, characterized by the fact that Mn is 1.11 to 1.45% by weight.
Petition 870190035569, of 15/04/2019, p. 26/34
2/4
[6]
6. Wear-resistant steel plate according to any one of claims 1 to 5, characterized by the fact that P is <0.009% by weight.
[7]
7. Wear-resistant steel plate according to any one of claims 1 to 6, characterized by the fact that S is <0.004% by weight.
[8]
Wear-resistant steel plate according to any one of claims 1 to 7, characterized in that Al is 0.021 to 0.039% by weight.
[9]
Wear-resistant steel plate according to any one of claims 1 to 8, characterized by the fact that Ti is 0.013 to 0.022% by weight.
[10]
10. Wear-resistant steel plate according to any one of claims 1 to 9, characterized by the fact that N is 0.0033 to 0.004% by weight.
[11]
11. Wear-resistant steel plate according to any one of claims 1 to 10, characterized by the fact that Ca is 0.001 to 0.003% by weight.
[12]
Wear-resistant steel plate according to any one of claims 1 to 11, characterized by the fact that Cr is 0.35 to 0.65% by weight.
[13]
13. Wear-resistant steel plate according to any one of claims 1 to 12, characterized by the fact that Ni is 0.16 to 0.40% by weight.
[14]
Wear-resistant steel plate according to any one of claims 1 to 13, characterized in that Mo is 0.18 - 0.24% by weight.
[15]
15. Wear-resistant steel sheet according to any one of claims 1 to 14, characterized in that the thickness of the sheet is 6 to 25 mm.
Petition 870190035569, of 15/04/2019, p. 27/34
3/4
[16]
16. Wear-resistant steel plate according to any one of claims 1 to 15, characterized by the fact that the Brinell hardness of it is> HB420.
[17]
17. Steel sheet production method, as defined in any one of claims 1 to 16, characterized by the fact that it comprises:
after vacuum degassing treatment, continuously cast or conventionally cast the molten steel and, if the molten steel is conventionally cast, laminate it in an ingot;
heat the continuous caster plate or ingot to a temperature of 1150 - 1250 ° C, and then laminate it in one pass or more than three passes in the austenite recrystallization zone, with the total reduction ratio being no less than 70% and the lamination termination temperature being not less than 860 ° C;
rapidly cool the laminated steel sheet at a speed of Vmin ~ 50 ° C / s to the temperature range of MS 145 ~ MS - 185 ° C, and then cool it in air to room temperature, where the hardening index P is calculated according to the expression
P = 2.7C + 0.4Si + Mn + 0.45Ni + 0.8Cr + 0.45Cu + 2Mo, the critical cooling speed Vmin to obtain martensite is calculated according to the expression lgVmin = 2.94 - 0, 75P, and the martensite formation temperature of MS is calculated according to the expression
Ms = 561 - 474C - 33Mn - 17Cr - 17Ni - 21Mo.
[18]
18. Method according to claim 17, characterized by the fact that the lamination termination temperature is 860 890 ° C.
[19]
19. Method according to claim 17 or 18, characterized by the fact that the rolled steel sheet is water-cooled
Petition 870190035569, of 15/04/2019, p. 28/34
4/4 quickly at a speed of 18 - 50 ° C / s up to the temperature range of 235 to 280 ° C.

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同族专利:

公开号 | 公开日

EP2784170A4|2016-04-13|

CN102560272A|2012-07-11|

JP2014520954A|2014-08-25|

US20140124102A1|2014-05-08|

WO2013075473A1|2013-05-30|

KR20140020351A|2014-02-18|

CA2837130C|2016-04-05|

EP2784170B1|2018-08-08|

CA2837130A1|2013-05-30|

BR112014000376A2|2017-02-14|

JP5833751B2|2015-12-16|

RU2593566C2|2016-08-10|

CN102560272B|2014-01-22|

RU2014110120A|2015-09-20|

US9695487B2|2017-07-04|

EP2784170A1|2014-10-01|

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法律状态:
2019-01-08| B06F| Objections, documents and/or translations needed after an examination request according art. 34 industrial property law|

2019-01-15| B06A| Notification to applicant to reply to the report for non-patentability or inadequacy of the application according art. 36 industrial patent law|

2019-05-14| B09A| Decision: intention to grant|

2019-07-02| B16A| Patent or certificate of addition of invention granted|Free format text: PRAZO DE VALIDADE: 20 (VINTE) ANOS CONTADOS A PARTIR DE 25/05/2012, OBSERVADAS AS CONDICOES LEGAIS. (CO) 20 (VINTE) ANOS CONTADOS A PARTIR DE 25/05/2012, OBSERVADAS AS CONDICOES LEGAIS |

优先权:

申请号 | 申请日 | 专利标题

CN201110383513.1|2011-11-25|

CN201110383513.1A|CN102560272B|2011-11-25|2011-11-25|Ultrahigh-strength abrasion-resistant steel plate and manufacturing method thereof|

PCT/CN2012/076058|WO2013075473A1|2011-11-25|2012-05-25|Steel plate with ultra-high strength and abrasion resistance, and manufacturing process thereof|

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