CN114774658B - Pipeline steel plate with uniform steel structure and preparation method thereof - Google Patents

Pipeline steel plate with uniform steel structure and preparation method thereof Download PDF

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Publication number
CN114774658B
CN114774658B CN202210453126.9A CN202210453126A CN114774658B CN 114774658 B CN114774658 B CN 114774658B CN 202210453126 A CN202210453126 A CN 202210453126A CN 114774658 B CN114774658 B CN 114774658B
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steel plate
finish
cooling
rolled steel
percent
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CN114774658A (en
Inventor
樊艳秋
马长文
李少坡
丁文华
赵新宇
张海
李战军
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Shougang Group Co Ltd
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Shougang Group Co Ltd
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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
    • 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
    • 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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/0081—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for slabs; for billets
    • 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
    • C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
    • 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
    • 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
    • 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
    • C22C38/16—Ferrous alloys, e.g. steel alloys containing copper
    • 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
    • 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
    • C21D2211/009—Pearlite

Abstract

The application relates to the technical field of pipeline steel plate preparation, in particular to a pipeline steel plate with uniform steel structure and a preparation method thereof, wherein the chemical components of the pipeline steel plate comprise the following components in percentage by mass: c is 0.04 to 0.10 percent, si:0.015 to 0.70 percent, mn:1% -2%, P: less than or equal to 0.010 percent, S: less than or equal to 0.001 percent, al:0.025% -0.035%, nb:0.0255% -0.045%, ti:0.0155 to 0.035 percent, cu:0.30 to 0.45 percent of Ni:0.2 to 0.5 percent, and the balance of Fe and unavoidable impurity elements; ni can enlarge the austenite region of iron, is a main alloy element for forming and stabilizing austenite, reduces the critical transition temperature and reduces the diffusion rate of each element in steel; meanwhile, through the combined action of the elements, the structural uniformity of the pipeline steel plate in the thickness direction is effectively ensured, and the hydrogen induced cracking resistance of the steel plate is more stable.

Description

Pipeline steel plate with uniform steel structure and preparation method thereof
Technical Field
The application relates to the technical field of pipeline steel plate preparation, in particular to a pipeline steel plate with uniform steel structure and a preparation method thereof.
Background
Hydrogen sulfide is a very corrosive medium in petroleum and natural gas, and the transportation pipeline is corroded by the medium in a large proportion during transportation. In a wet hydrogen sulfide environment, hydrogen bubbling, hydrogen cracking, etc. may occur in steel materials, and cracks generated by penetration of hydrogen generated by corrosion into a conveying pipe are called hydrogen cracking. Hydrogen induced cracking can not only cause environmental damage, but also can lead to huge property loss and casualties, and is potentially harmful. Therefore, the hydrogen induced cracking resistance is a very important performance index of steel sheet for pipeline.
Patent number CN109234618B, CN109594015a discloses an economical or low-cost HIC-resistant pipeline steel sheet X70MS, which focuses on the means of reducing alloy cost to reduce production cost, but none of them relates to a method for manufacturing thicker steel sheets and a level of Hydrogen Induced Cracking (HIC) resistance.
Disclosure of Invention
The application provides a pipeline steel plate with uniform steel structure and a preparation method thereof, which are used for solving the technical problem of poor stability of hydrogen induced cracking resistance in the pipeline steel plate.
In a first aspect, the present application provides a pipeline steel sheet having a uniform steel structure, the pipeline steel sheet comprising, in mass fractions: c is 0.04 to 0.10 percent, si:0.015 to 0.70 percent, mn:1% -2%, P: less than or equal to 0.010 percent, S: less than or equal to 0.001 percent, al:0.025% -0.035%, nb:0.0255% -0.045%, ti:0.0155 to 0.035 percent, cu:0.30 to 0.45 percent of Ni:0.2 to 0.5 percent, and the balance of Fe and unavoidable impurity elements;
optionally, the chemical components of the pipeline steel plate include, in mass fraction: c is 0.05 to 0.7 percent, si:0.055% -0.60%, mn:1.9 to 1.95 percent, P: less than or equal to 0.008 percent, S: less than or equal to 0.0008 percent, al:0.028% -0.032%, nb:0.0265% -0.035%, ti:0.0165% -0.025%, cu:0.32 to 0.35 percent of Ni:0.3 to 0.4 percent, and the balance of Fe and unavoidable impurity elements.
Optionally, the metallographic structure of the pipeline steel plate comprises 12-14% of pearlite and the balance of ferrite; the ferrite has a size of 1 to 15 μm.
Alternatively, the ferrite has an average size of 4-10 μm.
In a second aspect, the present application provides a method for producing a pipeline steel sheet according to the first aspect, the method comprising the steps of:
obtaining a plate blank;
performing first heating, rough rolling and finish rolling on the slab to obtain a finish rolled steel plate;
and performing first cooling, second heating and second cooling on the finish rolled steel plate to obtain the pipeline steel plate.
Optionally, the heat preservation temperature of the first heating is 1100-1200 ℃, and the heat preservation time of the first heating is 60-75 min.
Optionally, the initial temperature of the rough rolling is 1050-1100 ℃, the final temperature of the rough rolling is 950-1000 ℃, the initial temperature of the finish rolling is 850-900 ℃, and the final temperature of the finish rolling is 800-830 ℃.
Optionally, the end temperature of the first cooling is 100-150 ℃;
the first cooling includes a first stage and a second stage;
in the first stage, the finish rolled steel sheet includes, from a thickness direction: a first cooling layer, an intermediate cooling layer, and a second cooling layer, the intermediate cooling layer being located between the first cooling layer and the second cooling layer;
in the first stage, the first cooling layer and the second cooling layer are respectively cooled to a preset temperature at a speed of 70 ℃/s-80 ℃/s; and the intermediate cooling layer is cooled to the preset temperature at a speed of 25-32 ℃/s.
Optionally, in the second heating, the target temperatures of the upper surface and the lower surface of the finish rolled steel plate are respectively 400-450 ℃, and the target temperature of the middle part of the finish rolled steel plate is 340-380 ℃.
Optionally, the second cooling includes air cooling to room temperature.
Compared with the prior art, the technical scheme provided by the embodiment of the application has the following advantages:
the pipeline steel plate provided by the embodiment of the application is an economic low-carbon and low-alloy component system, wherein Ti is a strong carbide forming element and is enriched at a grain boundary, so that the growth of grains can be effectively inhibited, and the effect of refining the grains is achieved. Meanwhile, the growth of austenite grains can be organized in a welding heat affected zone; the Cu element can improve the strength and corrosion resistance, can improve the hardenability, is beneficial to the reinforcement of the hardenability of the middle part of the thick plate, and the Ni can enlarge the austenite region of iron, is a main alloy element for forming and stabilizing austenite, reduces the critical transition temperature and reduces the diffusion rate of each element in steel; through the combined action of the elements, the structural uniformity of the pipeline steel plate in the thickness direction is effectively ensured, and the hydrogen induced cracking resistance of the steel plate is more stable.
Drawings
The accompanying drawings, which are incorporated in and constitute a part of this specification, illustrate embodiments consistent with the invention and together with the description, serve to explain the principles of the invention.
In order to more clearly illustrate the embodiments of the invention or the technical solutions in the prior art, the following description will briefly explain the drawings used in the embodiments or the description of the prior art, and it will be obvious to those skilled in the art that other drawings can be obtained from these drawings without inventive effort.
Fig. 1 is a schematic flow chart of a method for preparing a pipeline steel plate with uniform steel structure according to an embodiment of the present application;
FIG. 2 is a metallographic structure diagram provided in example 1 of the present application;
fig. 3 is a metallographic structure diagram provided in comparative example 1 of the present application.
Detailed Description
For the purposes of making the objects, technical solutions and advantages of the embodiments of the present application more clear, the technical solutions of the embodiments of the present application will be clearly and completely described below with reference to the drawings in the embodiments of the present application, and it is apparent that the described embodiments are some embodiments of the present application, but not all embodiments. All other embodiments, which can be made by one of ordinary skill in the art without undue burden from the present disclosure, are within the scope of the present application based on the embodiments herein.
The application provides a pipeline steel plate with uniform steel structure, wherein the chemical components of the pipeline steel plate comprise the following components in percentage by mass: c is 0.04 to 0.10 percent, si:0.015 to 0.70 percent, mn:1% -2%, P: less than or equal to 0.010 percent, S: less than or equal to 0.001 percent, al:0.025% -0.035%, nb:0.0255% -0.045%, ti:0.0155 to 0.035 percent, cu:0.30 to 0.45 percent of Ni:0.2 to 0.5 percent, and the balance of Fe and unavoidable impurity elements.
The roles of the elements in this application are as follows:
the element C is one of means for improving strength, and if the content is too high, segregation occurs at the thickness center of the steel sheet, which has a very adverse effect on hydrogen induced cracking resistance and the like. In addition, the invention adds proper amount of Nb and Ti alloy elements to ensure the strength, so the ultralow carbon content is adopted, and the C content is controlled within the range of 0.04-0.1 percent.
Mn element can improve the strength of the steel plate, if the addition amount is too large, the Mn element is extremely easy to segregate at the thickness of the steel plate, the formation of a banded structure and a hard phase is promoted, the content is increased, the tendency of hydrogen induced cracking is increased, and the corrosion resistance of the material is deteriorated. In addition, it is also easily combined with S to form MnS inclusions, and increases the partial hydrogen pressure to become the easy place of hydrogen induced cracks. Therefore, comprehensively considering, mn is controlled in the range of 1-2.
The P and S elements are impurity elements in steel, are easy to segregate and influence the internal quality of the continuous casting billet. In order to obtain excellent hydrogen induced cracking resistance, the P, S content must be strictly controlled. The content control range of the invention is as follows: p: less than or equal to 0.010 percent, S: less than or equal to 0.001 percent.
Nb can raise the recrystallization temperature of austenite, expand the temperature range of unrecrystallized regions, delay unrecrystallized progress and effectively refine grains. The refined grains can not only improve the strength of the steel, but also improve the low-temperature toughness and the plasticity of the steel to a certain extent. The dispersion distribution of C, N compounds of the microalloy element Nb and the like on the matrix can also effectively refine grains. Thus, nb is controlled to 0.025-0.045%.
Ti is a strong carbide forming element and is enriched at a grain boundary, so that the growth of grains can be effectively inhibited, and the effect of refining the grains is achieved. Meanwhile, the growth of austenite grains can be organized in a welding heat affected zone, and the welding performance is improved. Therefore, ti is controlled to be within 0.015-0.035%.
The Cu element can improve the strength and corrosion resistance, and can also improve the hardenability, thereby being beneficial to the reinforcement of the hardenability of the core part of the thick plate. However, too high a Cu content may have a very adverse effect on impact properties, weldability, and the like. Therefore, cu is controlled to 0.30 to 0.45%.
Ni enlarges the austenitic region of iron and is the main alloying element that forms and stabilizes austenite. It can lower critical transition temperature, reduce the diffusion rate of each element in steel and raise hardenability. In addition, it can strengthen ferrite, refine and increase pearlite, improve strength and have no negative effect on toughness. Therefore, ni is controlled to 0.2 to 0.5.
As an alternative embodiment, the chemical composition of the pipeline steel plate includes, in mass fraction: c is 0.05 to 0.7 percent, si:0.055% -0.60%, mn:1.9 to 1.95 percent, P: less than or equal to 0.008 percent, S: less than or equal to 0.0008 percent, al:0.028% -0.032%, nb:0.0265% -0.035%, ti:0.0165% -0.025%, cu:0.32 to 0.35 percent of Ni:0.3 to 0.4 percent, and the balance of Fe and unavoidable impurity elements.
As an alternative embodiment, the metallographic structure of the pipeline steel plate comprises 12-14% pearlite and the balance ferrite; the ferrite has a size of 1 to 15 μm.
As an alternative embodiment, the ferrite has an average size of 4-10 μm.
In the embodiment of the application, the metallographic structure comprises 12-14% pearlite and the balance ferrite, and the structure type is favorable for hydrogen diffusion, so that the hydrogen induced cracking resistance is improved, and the ferrite has the advantages of reducing the internal stress of the steel plate and inhibiting crack growth, and the ferrite has the size of 1-15 mu m.
As an alternative embodiment, the hardness difference of the pipeline steel plate in the thickness direction is less than or equal to 70HV.
In the embodiment of the application, the hardness difference value of the pipeline steel plate in the thickness direction is less than or equal to 70HV, which indicates that the pipeline steel plate in the thickness direction has more uniform structure and is not easy to generate hydrogen induced cracking, the middle part of the pipeline steel plate in the thickness direction is conventionally the part of the pipeline steel plate which is about 3 cm to 25cm away from the upper surface and the lower surface, and the hardness of the middle part of the pipeline steel plate is less than or equal to 290HV, so that the pipeline steel plate has the beneficial effect of effectively avoiding crack nucleation; the hardness difference between the soft phase structure of the middle part and the hard phase structure of the middle part is less than or equal to 60HV, and the method has the beneficial effects of uniform structure and improvement of hydrogen induced cracking resistance.
In the embodiment of the application, the crack length rate, the crack thickness rate and the crack sensitivity rate are respectively 0, which indicates that the pipeline steel plate has stable performance and is not easy to crack.
In a second aspect, the present application provides a method for manufacturing a pipeline steel sheet according to the first aspect, as shown in fig. 1, the method comprising the steps of:
s1, obtaining a plate blank;
in this embodiment of the present application, the chemical components of the slab may be, in mass percentages: c is 0.04 to 0.10 percent, si:0.015 to 0.70 percent, mn:1% -2%, P: less than or equal to 0.010 percent, S: less than or equal to 0.001 percent, al:0.025% -0.035%, nb:0.0255% -0.045%, ti:0.0155 to 0.035 percent, cu:0.30 to 0.45 percent of Ni:0.2 to 0.5 percent, and the balance of Fe and unavoidable impurity elements.
S2, performing first heating, rough rolling and finish rolling on the plate blank to obtain a finish-rolled steel plate;
in an alternative embodiment, in the second heating, the target temperatures of the upper surface and the lower surface of the finish rolled steel plate are respectively 400-450 ℃, and the target temperature of the middle part of the finish rolled steel plate is 340-380 ℃.
S3, performing first cooling, second heating and second cooling on the finish-rolled steel plate to obtain the pipeline steel plate.
As an alternative embodiment, the end point temperature of the first cooling is 100 to 150 ℃;
in this embodiment of the present application, the reason for controlling the end temperature of the first cooling is to complete the sufficient transformation of the austenitic structure, control the structure type, if the temperature is higher than 150 ℃, the cooling time is shortened, and then the sufficiency of the transformation of the structure is affected, resulting in uneven structure type, and if the temperature is lower than 100 ℃, the cooling temperature is lower in a short time, the internal stress of the steel plate is increased, and cracks are easily formed.
The first cooling includes a first stage and a second stage;
in the first stage, the finish rolled steel sheet includes, from a thickness direction: a first cooling layer, an intermediate cooling layer, and a second cooling layer, the intermediate cooling layer being located between the first cooling layer and the second cooling layer;
in the first stage, the first cooling layer and the second cooling layer are respectively cooled to a preset temperature at a speed of 70 ℃/s-80 ℃/s; and the intermediate cooling layer is cooled to the preset temperature at a speed of 25-32 ℃/s.
In the embodiment of the application, the cooling is performed at a speed of 70 ℃/s to 80 ℃/s until the upper surface of the finish rolled steel plate is cooled to 400-450 ℃ in the first cooling layer and 1/4 of the thickness direction of the finish rolled steel plate; an intermediate cooling layer which cools the finish-rolled steel sheet from 1/4 of the thickness direction to 3/4 of the thickness direction at a rate of 25 ℃/s to 32 ℃/s to 340-380 ℃; a second cooling layer that cools the finish-rolled steel sheet from 3/4 th of the thickness direction to the lower surface of the finish-rolled steel sheet at a rate of 70 ℃/s to 80 ℃/s; the preset temperature may be 580 ℃.
In the embodiment of the application, the first cooling and the second heating control the tissue type, the proportion and the microhardness along the thickness direction of the steel plate more accurately, reduce the possibility of hydrogen induced cracking, and enable the steel plate to have excellent hydrogen induced cracking resistance.
In the embodiment of the application, the reason for controlling the cooling rate to 400-450 ℃ in the first cooling is to control the proportion of pearlite, so that the phenomenon of avoiding excessive proportion of pearlite and reducing the hydrogen induced cracking resistance is avoided, and the reason for selecting the cooling rate to 400-450 ℃ is to finely control the proportion of each phase in the tissue type; the reason why the cooling rate of the steel sheet portion 3 layers was controlled is to ensure uniformity of the structure in the thickness direction.
As an alternative embodiment, the second cooling includes air cooling to room temperature.
In this embodiment, the model of the pipeline steel plate may be X70, where X70 represents the strength grade of the steel plate.
As an alternative embodiment, the initial temperature of the rough rolling is 1050 to 1100 ℃, the final temperature of the rough rolling is 950 to 1000 ℃, the initial temperature of the finish rolling is 850 to 900 ℃, and the final temperature of the finish rolling is 800 to 830 ℃.
As an alternative embodiment, the temperature of the first heating is 1100-1200 ℃, and the temperature of the first heating is 60-75 min.
As an alternative embodiment, the initial temperature of the rough rolling is 1050 to 1100 ℃, the final temperature of the rough rolling is 950 to 1000 ℃, the initial temperature of the finish rolling is 850 to 900 ℃, and the final temperature of the finish rolling is 800 to 830 ℃.
The method of the present invention will be described in detail with reference to examples, comparative examples and experimental data.
Examples 1 to 5 and comparative example 1
In examples 1 to 5 and comparative example 1, slabs having the chemical components (balance of Fe and unavoidable impurities) shown in table 1 were heated to 1100 to 1200 ℃, and then rough rolled, finish rolled and water cooled to obtain steel sheets having ferrite+pearlite structure.
The control of the process parameters of heating, rough rolling, finish rolling and cooling in the production process are shown in tables 2 and 3.
The steel sheet was sampled and subjected to mechanical property detection, and the detection results are shown in table 4.
The steel sheet was sampled and tested for hydrogen induced cracking resistance, and the test results are shown in table 5.
Table 1 chemical compositions of the pipeline steel sheets of examples 1 to 5 and comparative examples.
Table 2 the process for preparing the pipeline steel sheets of examples 1 to 5 and comparative examples.
Table 3 first cooling and second heating processes of the pipeline steel sheets of examples 1 to 5 and comparative examples.
Table 4 mechanical properties of the pipeline steel sheets of examples 1 to 5 and comparative examples.
Table 5 cracking properties of the pipeline steel sheets of examples 1 to 5 and comparative examples.
Numbering device Crack length rate/% Crack thickness rate/% Crack sensitivity/%
Example 1 0 0 0
Example 2 0 0 0
Example 3 0 0 0
Example 4 0 0 0
Example 5 0 0 0
Comparative example 1 25 7 3
As can be seen from Table 4, the yield strength of the example group is greater than 480Mpa, the tensile strength is greater than 600Mpa, the Charpy impact energy at-10 ℃ is greater than 400J, and the hardness difference of the pipeline steel plates in the thickness direction is less than or equal to 70HV; the hardness of the middle part of the pipeline steel plate in the thickness direction is less than or equal to 290HV, which indicates that the steel plate has excellent performance, uniform structure and difficult occurrence of hydrogen induced cracking; in comparative example 1, the yield strength was less than 430MPa, the tensile strength was less than 600MPa, and the difference in hardness in the thickness direction was 80HV; the hardness of the middle part of the pipeline steel plate in the thickness direction is higher than 300HV, which indicates that the steel plate of the comparative example is insufficient in strength and uneven in structure in the thickness direction; as can be seen from Table 5, the pipeline steel plate has excellent cracking resistance, but the comparative example 1 has poor hydrogen induced cracking resistance, and does not meet the use requirement, FIG. 2 is a metallographic structure diagram of example 1, and FIG. 3 is a metallographic structure diagram of comparative example 1, which shows that the steel plate has different mechanical properties and cracking resistance from the steel plate of comparative example 1.
It should be noted that in this document, relational terms such as "first" and "second" and the like are used solely to distinguish one entity or action from another entity or action without necessarily requiring or implying any actual such relationship or order between such entities or actions. Moreover, the terms "comprises," "comprising," or any other variation thereof, are intended to cover a non-exclusive inclusion, such that a process, method, article, or apparatus that comprises a list of elements does not include only those elements but may include other elements not expressly listed or inherent to such process, method, article, or apparatus. Without further limitation, an element defined by the phrase "comprising one … …" does not exclude the presence of other like elements in a process, method, article, or apparatus that comprises the element.
The foregoing is only a specific embodiment of the invention to enable those skilled in the art to understand or practice the invention. Various modifications to these embodiments will be readily apparent to those skilled in the art, and the generic principles defined herein may be applied to other embodiments without departing from the spirit or scope of the invention. Thus, the present invention is not intended to be limited to the embodiments shown herein but is to be accorded the widest scope consistent with the principles and novel features disclosed herein.

Claims (5)

1. A pipeline steel plate with uniform steel structure, characterized in that the chemical components of the pipeline steel plate comprise the following components in mass fraction: c is 0.05% -0.7%, si:0.055% -0.60%, mn:1.9% -1.95%, P: less than or equal to 0.008 percent, S: less than or equal to 0.0008 percent, al:0.028% -0.032%, nb:0.0265% -0.035%, ti:0.0165% -0.025%, cu:0.32% -0.35%, ni:0.3% -0.4%, and the balance being Fe and unavoidable impurity elements, wherein the metallographic structure of the pipeline steel plate comprises 12% -14% pearlite and the balance being ferrite; the ferrite has a size of 1-15 mu m, the average size of the ferrite is 4-10 mu m, and the preparation method of the pipeline steel plate comprises the following steps:
obtaining a plate blank;
performing first heating, rough rolling and finish rolling on the slab to obtain a finish rolled steel plate;
performing first cooling, second heating and second cooling on the finish-rolled steel plate to obtain a pipeline steel plate;
the end temperature of the first cooling is 100-150 ℃;
the first cooling includes a first stage and a second stage;
in the first stage, the finish rolled steel sheet includes, from a thickness direction: a first cooling layer, an intermediate cooling layer, and a second cooling layer, the intermediate cooling layer being located between the first cooling layer and the second cooling layer; cooling to 400-450 ℃ in the first cooling layer, namely cooling from the upper surface of the finish-rolled steel plate to 1/4 of the thickness direction of the finish-rolled steel plate at a speed of 70-80 ℃/s; an intermediate cooling layer, wherein the cooling is carried out at a speed of 25 ℃/s-32 ℃/s from 1/4 of the thickness direction of the finish-rolled steel plate to 3/4 of the thickness direction of the finish-rolled steel plate to 340-380 ℃; a second cooling layer which cools the 3/4 part of the thickness direction of the finish-rolled steel plate to the lower surface of the finish-rolled steel plate at a speed of 70-80 ℃/s;
in the second heating, the target temperatures of the upper surface and the lower surface of the finish rolling steel plate are 400-450 ℃ respectively, and the target temperature of the middle part of the finish rolling steel plate is 340-380 ℃.
2. A method for producing a pipeline steel sheet as claimed in claim 1, comprising the steps of:
obtaining a plate blank;
performing first heating, rough rolling and finish rolling on the slab to obtain a finish rolled steel plate;
performing first cooling, second heating and second cooling on the finish-rolled steel plate to obtain a pipeline steel plate;
the end temperature of the first cooling is 100-150 ℃;
the first cooling includes a first stage and a second stage;
in the first stage, the finish rolled steel sheet includes, from a thickness direction: a first cooling layer, an intermediate cooling layer, and a second cooling layer, the intermediate cooling layer being located between the first cooling layer and the second cooling layer; cooling to 400-450 ℃ in the first cooling layer, namely cooling from the upper surface of the finish-rolled steel plate to 1/4 of the thickness direction of the finish-rolled steel plate at a speed of 70-80 ℃/s; an intermediate cooling layer, wherein the cooling is carried out at a speed of 25 ℃/s-32 ℃/s from 1/4 of the thickness direction of the finish-rolled steel plate to 3/4 of the thickness direction of the finish-rolled steel plate to 340-380 ℃; a second cooling layer which cools the 3/4 part of the thickness direction of the finish-rolled steel plate to the lower surface of the finish-rolled steel plate at a speed of 70-80 ℃/s;
in the second heating, the target temperatures of the upper surface and the lower surface of the finish rolling steel plate are 400-450 ℃ respectively, and the target temperature of the middle part of the finish rolling steel plate is 340-380 ℃.
3. The method according to claim 2, wherein the first heating is performed at a holding temperature of 1100-1200 ℃ and a holding time of 60-75 min.
4. The method according to claim 2, wherein the initial temperature of the rough rolling is 1050-1100 ℃, the final temperature of the rough rolling is 950-1000 ℃, the initial temperature of the finish rolling is 850-900 ℃, and the final temperature of the finish rolling is 800-830 ℃.
5. The method of claim 2, wherein the second cooling comprises air cooling to room temperature.
CN202210453126.9A 2022-04-27 2022-04-27 Pipeline steel plate with uniform steel structure and preparation method thereof Active CN114774658B (en)

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Publication number Priority date Publication date Assignee Title
JP2010196160A (en) * 2009-01-30 2010-09-09 Jfe Steel Corp Heavy gauge high tensile strength hot rolled steel sheet with excellent hic resistance, and manufacturing method therefor
CN101928885A (en) * 2009-06-26 2010-12-29 上海梅山钢铁股份有限公司 Hydrothion corrosion resistant pipe steel and production method thereof
CN103526129A (en) * 2013-09-27 2014-01-22 济钢集团有限公司 Thick-specification acid-corrosion-resisting X65 pipeline steel plate and manufacturing method thereof
JP2017057449A (en) * 2015-09-15 2017-03-23 新日鐵住金株式会社 Steel sheet excellent in sour resistance and production method therefor
CN108342655A (en) * 2017-01-22 2018-07-31 宝山钢铁股份有限公司 A kind of quenching and tempering type acid-resistant pipeline steel and its manufacturing method
CN114318159A (en) * 2021-12-02 2022-04-12 首钢集团有限公司 345 MPa-grade container steel plate with hydrogen induced cracking resistance and preparation method thereof

Patent Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2010196160A (en) * 2009-01-30 2010-09-09 Jfe Steel Corp Heavy gauge high tensile strength hot rolled steel sheet with excellent hic resistance, and manufacturing method therefor
CN101928885A (en) * 2009-06-26 2010-12-29 上海梅山钢铁股份有限公司 Hydrothion corrosion resistant pipe steel and production method thereof
CN103526129A (en) * 2013-09-27 2014-01-22 济钢集团有限公司 Thick-specification acid-corrosion-resisting X65 pipeline steel plate and manufacturing method thereof
JP2017057449A (en) * 2015-09-15 2017-03-23 新日鐵住金株式会社 Steel sheet excellent in sour resistance and production method therefor
CN108342655A (en) * 2017-01-22 2018-07-31 宝山钢铁股份有限公司 A kind of quenching and tempering type acid-resistant pipeline steel and its manufacturing method
CN114318159A (en) * 2021-12-02 2022-04-12 首钢集团有限公司 345 MPa-grade container steel plate with hydrogen induced cracking resistance and preparation method thereof

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