CN115595505A - 600 MPa-grade axle housing steel with high temperature resistance and high hole expansion rate and production method thereof - Google Patents
600 MPa-grade axle housing steel with high temperature resistance and high hole expansion rate and production method thereof Download PDFInfo
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 67
- 239000010959 steel Substances 0.000 title claims abstract description 67
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 23
- 238000005096 rolling process Methods 0.000 claims abstract description 38
- 238000001816 cooling Methods 0.000 claims abstract description 23
- 238000010438 heat treatment Methods 0.000 claims abstract description 18
- 229910001563 bainite Inorganic materials 0.000 claims abstract description 14
- 229910000859 α-Fe Inorganic materials 0.000 claims abstract description 14
- 238000002791 soaking Methods 0.000 claims abstract description 10
- 229910052698 phosphorus Inorganic materials 0.000 claims abstract description 9
- 239000012535 impurity Substances 0.000 claims abstract description 8
- 239000000126 substance Substances 0.000 claims abstract description 8
- 229910052721 tungsten Inorganic materials 0.000 claims abstract description 5
- 238000005266 casting Methods 0.000 claims description 6
- 238000003723 Smelting Methods 0.000 claims description 3
- 239000011159 matrix material Substances 0.000 abstract description 3
- 238000005098 hot rolling Methods 0.000 abstract description 2
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- 238000000034 method Methods 0.000 description 9
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- 230000008569 process Effects 0.000 description 6
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- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 description 2
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- 206010020751 Hypersensitivity Diseases 0.000 description 1
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- KSOKAHYVTMZFBJ-UHFFFAOYSA-N iron;methane Chemical compound C.[Fe].[Fe].[Fe] KSOKAHYVTMZFBJ-UHFFFAOYSA-N 0.000 description 1
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Classifications
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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
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
- B21B1/22—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length
- B21B1/24—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length in a continuous or semi-continuous process
- B21B1/26—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length in a continuous or semi-continuous process by hot-rolling, e.g. Steckel hot mill
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B37/00—Control devices or methods specially adapted for metal-rolling mills or the work produced thereby
- B21B37/74—Temperature control, e.g. by cooling or heating the rolls or the product
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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
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
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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
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0226—Hot rolling
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/002—Bainite
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/005—Ferrite
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Heat Treatment Of Steel (AREA)
Abstract
The invention discloses 600 MPa-grade axle housing steel with high temperature resistance and high hole expansion rate and a production method thereof, wherein the axle housing steel comprises the following chemical components in percentage by weight: c:0.03 to 0.06%, si:0.60 to 1.00%, mn: 1.60-2.00%, P is less than or equal to 0.020%, S is less than or equal to 0.010%, als:0.02 to 0.06%, nb:0.020 to 0.050%, W:0.05 to 0.20 percent, and the balance of Fe and impurities. The production method comprises the following steps: 1) Controlling the temperature of the second heating section and the temperature of the soaking end section to be 1220-1280 ℃, wherein the heating time and the soaking time are not less than 70min, and the total in-furnace time is controlled to be not less than 160min; 2) Controlling the outlet temperature of rough rolling to be 1060-1100 ℃; 3) Controlling the initial rolling temperature of finish rolling to be 1000-1050 ℃, and the finish rolling temperature of finish rolling to be 860-900 ℃; 4) The front section is cooled to 580-630 ℃ at the cooling speed of 20-40 ℃/s; then, a laminar flow mode is adopted, and the steel is cooled to the coiling temperature at the cooling speed of 5-10 ℃/s; 5) The coiling temperature is controlled between 480 and 580 ℃. The axle housing steel has the yield strength of more than or equal to 500MPa, the tensile strength of more than or equal to 600MPa, the elongation A of more than or equal to 20 percent and the hole expansion rate of more than or equal to 90 percent, a steel matrix forms a ferrite and bainite dual-phase structure, the yield strength is ensured to be more than or equal to 500MPa after heating at 850 ℃/20min, and the hot rolling production is simple and easy to control.
Description
Technical Field
The invention belongs to the technical field of axle housing steel processing, and particularly relates to 600 MPa-grade axle housing steel with high temperature resistance and high hole expansion rate and a production method thereof.
Background
The steel for the automobile axle housing is used as an important component of a chassis system of three large assemblies of a commercial automobile, the consumption of the steel plate accounts for about 4 percent of the consumption of the steel plate of the whole automobile at present, and the driving axle housing has enough strength and rigidity and good plasticity and toughness. The truck axles are mostly made of steel plates which are formed by cold stamping or hot stamping, so that the steel plates are required to have good high yield strength performance and high hole expansion forming rate after being formed by cold stamping and hot stamping.
Chinese patent publication No. CN104213019A discloses a document of 600MPa grade automobile axle housing steel and a production method thereof. In the technical solution disclosed in this patent document, the chemical composition contains, in mass percent, C:0.21% -0.26%; si:0.51% -0.6%; mn:1.1 to 1.5 percent; al:0.01 to 0.06 percent; p: less than or equal to 0.02 percent; s: less than or equal to 0.01 percent; v:0.05% -0.06%; n:0.012% -0.016%; the balance of Fe and inevitable impurities, wherein V: n is less than or equal to 5:1. the hot rolled strip steel for the 600 MPa-grade automobile axle housing is finally obtained by controlling the content of V and N elements and rolling and cooling. The method comprises the following steps: the content of C is higher, the forming performance is poorer, and the quality problems such as cracking and the like are easy to occur in the forming process of the automobile axle housing.
Chinese patent publication No. CN105239013A discloses a document of "an axle housing steel for cold forming and a manufacturing method thereof". In the technical solution disclosed in this patent document, the chemical components include, in mass percent, 0.08 to 0.18% of C, 0.10 to 0.45% of Si, mn:1.2 to 2.5 percent of Ti, 0.01 to 0.05 percent of Ti, 0.02 to 0.35 percent of Al, less than or equal to 0.02 percent of P, less than or equal to 0.010 percent of S, 0.02 to 0.10 percent of V, 0.015 to 0.10 percent of Nb, 0.02 to 0.5 percent of Cr, and the balance of Fe and inevitable impurities. The cost is reduced, the welding performance of the axle housing steel for cold forming is guaranteed, and the 600 MPa-grade automobile axle housing steel plate is finally obtained. Although the content of C, si in the design of the method is not high, the Ti content is required to be in the range of 0.01-0.05%, the control of the content of effective titanium in steel is easy to fluctuate, and the mechanical property of a steel plate can be greatly fluctuated; the metallographic structure is ferrite and pearlite, the workpiece is easy to crack in cold stamping forming, and the yield strength of the material after high-temperature heating forming can not be ensured to be more than 500MPa.
Chinese patent publication No. CN110079740A discloses a document of 'high-toughness hot-rolled 530 MPa-grade automobile cold-stamped axle housing steel plate and a manufacturing method thereof'. The Mn content is properly increased without adding V in the component design, and a certain amount of Si, nb, ti and the like are added, so that the surface quality and the strength of the steel meet the cold stamping and welding processing of the axle housing steel; the yield strength ReL is more than or equal to 375MPa, the tensile strength Rm is more than or equal to 530MPa, the elongation A after fracture is more than or equal to 26 percent, the impact energy KV2 at 0 ℃ is more than or equal to 180J, the grain size is 8-10 grade, the belt grade is 1-3 grade, and the cold stamping processing forming of 10-16 mm specification can be realized. The method comprises the following steps: the C content is required to be 0.12-0.16, the peritectic steel belongs to peritectic steel, the quality defect of a casting blank is easy to generate, and the yield is relatively low; the metallographic structure is ferrite and pearlite, the strength is low, and the cracking phenomenon is easy to occur in cold stamping deformation.
The existing axle housing steel with the tensile strength reaching 600MPa level has the technical problems of high carbon content, yield strength lower than 500MPa after long-time high-temperature heating and the like, and can not be suitable for various high-end axle housing forming processes and the requirements of light weight of automobile axle housings.
Disclosure of Invention
In order to solve the technical problems, the invention aims to overcome the defects that the metallographic structure of the axle housing steel with the tensile strength of 600MPa in the prior art is ferrite plus pearlite, so that the carbon content is high, and the workpiece is easy to crack during cold and hot forming, and provides the hot continuous rolling axle housing steel and the production method, wherein the yield strength of the axle housing steel after being heated at high temperature is ensured to be more than 500MPa, the production difficulty of a steel plate is low, and the plasticity of the steel plate is excellent.
In order to achieve the purpose, the technical scheme of the invention is as follows:
on one hand, the invention provides 600 MPa-grade axle housing steel with high temperature resistance and high hole expansibility, which comprises the following chemical components in percentage by weight: c:0.03 to 0.06%, si:0.60 to 1.00%, mn: 1.60-2.00%, P is less than or equal to 0.020%, S is less than or equal to 0.010%, als:0.02 to 0.06%, nb:0.020 to 0.050%, W:0.05 to 0.20 percent, and the balance of Fe and impurities; the metallographic structure of the axle housing steel is ferrite and bainite.
Preferably, the axle housing steel comprises the following chemical components in percentage by weight: c: 0.032-0.58%, si:0.62 to 0.92%, mn: 1.66-1.89%, P is less than or equal to 0.020%, S is less than or equal to 0.010%, als:0.02 to 0.06%, nb:0.020 to 0.050%, W: 0.06-0.19 percent, and the balance of Fe and impurities.
In another aspect, the invention provides a method for producing 600MPa axle housing steel with high temperature resistance and high hole expansibility, comprising the following steps:
1) Heating a casting blank after smelting and pouring to form a blank:
controlling the temperature of the second heating section and the temperature of the soaking end section to be 1220-1280 ℃, wherein the heating time and the soaking time are not less than 70min, and the total in-furnace time is controlled to be not less than 160min;
2) Carrying out rough rolling: controlling the outlet temperature of rough rolling to be 1060-1100 ℃;
3) Carrying out finish rolling: controlling the initial rolling temperature of finish rolling to be 1000-1050 ℃, and the finish rolling temperature of finish rolling to be 860-900 ℃;
4) And (3) cooling: the front section is cooled to 580-630 ℃ at the cooling speed of 20-40 ℃/s; then, a laminar flow mode is adopted, and the steel is cooled to the coiling temperature at the cooling speed of 5-10 ℃/s;
5) Coiling: the coiling temperature is controlled between 480 and 580 ℃.
Preferably, the rough rolling outlet temperature is 1060 to 1095 ℃.
Preferably, the finishing temperature of the finish rolling is 861-896 ℃.
Preferably, the temperature after the front section cooling is finished is 588-629 ℃.
Preferably, the coiling temperature is 486-576 ℃.
The invention relates to 600 MPa-grade axle housing steel with high temperature resistance and high hole expansion rate and a production method thereof, and the technical principle is as follows:
c plays a role in solid solution strengthening, and when the content of C is less than 0.06%, the steel is subjected to high-temperature austenitization and cooling after thermal deformation, the two-phase decomposition of austenite to ferrite and cementite is less generated, and the toughness of the bainite in the form is excellent. Comprehensively considering, the weight percentage of C is preferably 0.03-0.06%.
Si: si is an important reduction and deoxidation element in the steelmaking process, can be dissolved in ferrite and austenite to improve the hardness and strength of steel; the ferrite crystal grains can be promoted to crystallize, and the coercive force is reduced; when the steel containing Si element is heated in an oxidizing atmosphere, a layer of SiO2 film is formed on the surface, and the oxidation resistance of the steel at high temperature is improved. When the content of Si exceeds 3%, the plasticity and toughness of the steel are obviously reduced, and the weight percentage of Si is preferably 0.60-1.00%.
Mn: mn is an effective element for improving the strength and the toughness, has a larger promotion effect on bainite transformation, has a more obvious effect under the condition of low carbon, and is low in cost, and the Mn content of 1.60-2.00 percent by weight is suitable for comprehensive consideration.
Al: al is a deoxidizing element and can be used as an AlN forming element to effectively refine crystal grains, and the effect is small when the content of Al is less than 0.01 percent; when the content exceeds 0.07%, the deoxidation effect is saturated; comprehensively considering, the weight percentage of Als is preferably 0.02-0.06%.
Nb: nb atoms can be dissolved in an austenite matrix in a solid mode, and tend to be segregated on grain boundaries due to size effect, and the segregation can block the movement of new grain boundaries recrystallized after austenite deformation, so that grains can be greatly refined. In the cooling process after high-temperature deformation, the segregation of Nb atoms in the grain boundary greatly prevents a new phase from nucleating at the grain boundary, so that a proeutectoid ferrite generation region is shifted to the right, and a uniform bainite structure can be obtained in a wide cooling speed range. In comprehensive consideration, the weight percentage of Nb is preferably 0.020-0.050%.
W: w is metal with the highest melting point, the formed WC has high hardness, the function in steel is similar to that of molybdenum, but the function of heat allergy resistance is better than that of molybdenum, and when the content of W is less than 0.05%, the effect is slight; when the content exceeds 0.20%, brittleness increases; in comprehensive consideration, the weight percentage of W is preferably 0.05-0.20%.
P, S: p, S is a harmful impurity element in steel, P in steel is easy to form segregation in steel, cold brittleness of steel plate is increased, S is easy to form plastic sulfide, steel plate is layered, hot brittleness of steel plate is increased, therefore, the lower the content of P, S is, the better, comprehensively considering that the content of P, S in steel is P less than or equal to 0.020%, and S less than or equal to 0.010%.
The invention controls the temperature of the second heating section and the soaking tail section to be 1220-1280 ℃, the heating and soaking time to be not less than 70min, and the total furnace time to be not less than 160min, so as to ensure complete solid solution and full austenitization of alloy elements, control the fineness of original austenite grains and ensure the uniform temperature of a plate blank.
The invention controls the rough rolling outlet temperature to be 1060-1100 ℃ in order to control the temperature of a recrystallization zone so as to obtain refined austenite grains.
The invention controls the rolling start temperature of the finish rolling to be 1000-1050 ℃, and the finish rolling temperature of the finish rolling to be 860-900 ℃ in order to control the rolling in the non-recrystallization area to obtain finer grain structure, reduce the load of the finish rolling, ensure the uniformity of plastic deformation and obtain better rolled plate shape.
The front section of the invention is cooled to 580-630 ℃ at the cooling speed of 20-40 ℃/s; and then cooling by adopting a laminar flow mode, wherein the cooling is carried out to the coiling temperature at a cooling speed of 5-10 ℃/s because the ultrafast cooling section can extremely refine the grain structure and then keep in a bainite transformation temperature interval to obtain a uniform low-carbon bainite grain structure.
The invention controls the coiling temperature to be 480-580 ℃, in order to avoid martensite or polygonal ferrite structure with poor toughness, a low-carbon bainite + acicular ferrite structure is obtained in the range, and finally an F + B dual-phase structure with excellent plasticity is formed.
Compared with the prior art, the invention has the following advantages:
compared with the prior art, the yield strength of the steel is more than or equal to 500MPa, the tensile strength is more than or equal to 600MPa, the elongation A is more than or equal to 20 percent, the hole expansion rate is more than or equal to 90 percent, a ferrite and bainite dual-phase structure is formed on a steel matrix, the yield strength is more than or equal to 500MPa after heating at 850 ℃/20min, and the hot rolling production is simple and easy to control.
Drawings
FIG. 1 is a metallographic structure diagram of 600MPa axle housing steel with high temperature resistance and high hole expansibility.
Detailed Description
In order that those skilled in the art will better understand the technical solutions of the present invention, the following description of the preferred embodiments of the present invention is provided in connection with specific examples, which should not be construed as limiting the present patent.
The test methods or test methods described in the following examples are conventional methods unless otherwise specified; the reagents and materials, unless otherwise indicated, are conventionally obtained commercially or prepared by conventional methods.
The invention will be described in detail below with reference to fig. 1 and several embodiments:
table 1 is a list of values of the components of each example and comparative example of the present invention;
table 2 shows the values of the process parameters of the examples and comparative examples of the present invention;
table 3 is a table of the results of testing the performance of each example and comparative example of the present invention.
The preparation method comprises the following steps:
1) Heating a casting blank after smelting and casting to form a blank: controlling the temperature of the second heating section and the temperature of the soaking end section to be 1220-1280 ℃, wherein the heating time and the soaking time are not less than 70min, and the total in-furnace time is controlled to be not less than 160min;
2) Rough rolling is carried out, and the outlet temperature of the rough rolling is controlled to be 1060-1100 ℃;
3) Carrying out finish rolling, wherein the start rolling temperature of the finish rolling is controlled to be 1000-1050 ℃, and the finish rolling temperature is 860-900 ℃;
4) And (3) cooling: the front section is cooled to 580-630 ℃ at the cooling speed of 20-40 ℃/s; then, a laminar flow mode is adopted, and the steel is cooled to the coiling temperature at the cooling speed of 5-10 ℃/s, because the ultra-fast cooling section can extremely refine the grain structure, and then the steel is kept in a bainite transformation temperature interval, so that uniform low-carbon bainite grain structure is obtained.
5) Coiling is carried out, and the coiling temperature is controlled to be 480-580 ℃.
TABLE 1 tabulated (wt%) chemical composition values for each example of the invention and comparative example
TABLE 2 values of the process parameters of the examples and comparative examples of the invention
TABLE 3 List of the results of testing the performance of the inventive and comparative examples
Note: table 3 was tested according to the national standards GB/T228 and GB/T231.
As can be seen from Table 3, in the 10 processes of the embodiment of the invention, the yield strength is more than or equal to 500MPa, the tensile strength is more than or equal to 600MPa, the elongation A is more than or equal to 20%, the hole expansion rate is more than or equal to 90%, and the yield strength after 850 ℃/20min hot working is more than or equal to 500MPa. In the comparative example 1, the metallographic phase is a bainite structure, the elongation is low, the hole expansion rate is low, and the yield strength is only 462MPa after 850 ℃/20min hot working; in comparative example 2, the metallographic phase is a ferrite plus pearlite structure, the carbon content is high, the yield strength is low, the hole expansion rate is low, and the yield strength is only 415MPa after 850 ℃/20min hot working.
As shown in figure 1, the metallographic phase of the embodiment of the invention is a ferrite and bainite structure, the carbon equivalent is low, the hole expansion rate is more than or equal to 90 percent, the forming performance is excellent, and the yield strength is more than or equal to 500MPa after heating at 850 ℃/20 min.
The above are only preferred embodiments of the present invention, and it should be noted that the above preferred embodiments should not be considered as limiting the present invention, and the protection scope of the present invention should be subject to the scope defined by the claims. It will be apparent to those skilled in the art that various modifications and adaptations can be made without departing from the spirit and scope of the invention, and these modifications and adaptations should be considered within the scope of the invention.
Claims (7)
1. The 600 MPa-grade axle housing steel with high temperature resistance and high hole expansibility is characterized in that the axle housing steel comprises the following chemical components in percentage by weight: c:0.03 to 0.06%, si:0.60 to 1.00%, mn: 1.60-2.00%, P is less than or equal to 0.020%, S is less than or equal to 0.010%, als:0.02 to 0.06%, nb:0.020 to 0.050%, W:0.05 to 0.20 percent, and the balance of Fe and impurities; the metallographic structure of the axle housing steel is ferrite and bainite.
2. The 600MPa grade axle housing steel with high temperature resistance and high hole expansibility as claimed in claim 1, wherein: the axle housing steel comprises the following chemical components in percentage by weight: c: 0.032-0.58%, si:0.62 to 0.92%, mn: 1.66-1.89%, P is less than or equal to 0.020%, S is less than or equal to 0.010%, als:0.02 to 0.06%, nb:0.020 to 0.050%, W:0.06 to 0.19 percent, and the balance of Fe and impurities.
3. A method for producing the 600MPa axle housing steel with high temperature resistance and high hole expansibility of claim 1, which comprises the following steps:
1) Heating a casting blank after smelting and casting to form a blank:
controlling the temperature of the second heating section and the temperature of the soaking end section to be 1220-1280 ℃, wherein the heating time and the soaking time are not less than 70min, and the total furnace time is controlled to be not less than 160min;
2) Carrying out rough rolling: controlling the outlet temperature of rough rolling to be 1060-1100 ℃;
3) Carrying out finish rolling: controlling the initial rolling temperature of finish rolling to be 1000-1050 ℃, and the finish rolling temperature of finish rolling to be 860-900 ℃;
4) And (3) cooling: the front section is cooled to 580-630 ℃ at the cooling speed of 20-40 ℃/s; then, a laminar flow mode is adopted, and the steel is cooled to the coiling temperature at the cooling speed of 5-10 ℃/s;
5) Coiling: the coiling temperature is controlled between 480 and 580 ℃.
4. The production method of the 600 MPa-grade axle housing steel with high temperature resistance and high hole expansibility as claimed in claim 3, wherein the production method comprises the following steps: the outlet temperature of the rough rolling is 1060-1095 ℃.
5. The production method of the 600 MPa-grade axle housing steel with high temperature resistance and high hole expansibility as claimed in claim 3, wherein the production method comprises the following steps: the finishing temperature of the finish rolling is 861-896 ℃.
6. The production method of the 600 MPa-grade axle housing steel with high temperature resistance and high hole expansibility as claimed in claim 3, wherein the production method comprises the following steps: the temperature is 588-629 ℃ after the front section cooling is finished.
7. The production method of the 600 MPa-grade axle housing steel with high temperature resistance and high hole expansibility as claimed in claim 3, wherein the production method comprises the following steps: the coiling temperature is 486-576 ℃.
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