CN114921721B - Pipeline steel plate with excellent hydrogen induced cracking resistance and preparation method thereof - Google Patents
Pipeline steel plate with excellent hydrogen induced cracking resistance and preparation method thereof Download PDFInfo
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- CN114921721B CN114921721B CN202210455726.9A CN202210455726A CN114921721B CN 114921721 B CN114921721 B CN 114921721B CN 202210455726 A CN202210455726 A CN 202210455726A CN 114921721 B CN114921721 B CN 114921721B
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- 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
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
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- C—CHEMISTRY; METALLURGY
- 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
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/005—Ferrite
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/009—Pearlite
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Abstract
The application relates to the technical field of pipeline steel plate preparation, in particular to a pipeline steel plate with excellent hydrogen induced cracking resistance and a preparation method thereof; the chemical components of the pipeline steel plate comprise the following components in percentage by mass: c:0.08 to 0.10 percent, si:0.01 to 0.70 percent, mn:0.8% -1.8%, P: less than or equal to 0.010 percent, S: less than or equal to 0.001 percent, al:0.025% -0.035%, nb:0.05 to 0.07 percent of Ti:0.03 to 0.05 percent of Cu:0.1 percent of 5 to 0.3 percent, and the balance of Fe and unavoidable impurity elements; the thickness of the pipeline steel plate is 15-45 mm. The method adopts an economic low-carbon and low-alloy component system, has proper carbon content, does not generate segregation, and has hydrogen induced cracking resistance; ti is enriched at the grain boundary, so that the growth of grains can be effectively inhibited, and the grains are refined; nb can raise the recrystallization temperature of austenite, expand the temperature range of the recrystallization zone, delay the recrystallization, and refine grains; the comprehensive effect of each element improves the tissue uniformity of the medium-thickness pipeline steel plate; by combining the rolling and cooling processes, the pipeline steel plate has a uniform metallographic structure, and the problem that the medium-thickness pipeline steel plate is easy to generate hydrogen-induced cracks is avoided.
Description
Technical Field
The application relates to the technical field of pipeline steel plate preparation, in particular to a pipeline steel plate with excellent hydrogen induced cracking resistance and a preparation method thereof.
Background
Hydrogen sulfide is a medium with very corrosive action in petroleum and natural gas, and the corrosion of the steel plate of the conveying pipeline by the medium accounts for a large proportion in the transportation process. In a wet hydrogen sulfide environment, hydrogen bubbling, hydrogen cracking, etc. may occur in a pipeline steel sheet, 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 the steel sheet for pipelines, and the factors influencing the hydrogen induced cracking are many, mainly including organization type, inclusion, center segregation, precipitation and the like.
The patent number CN111235489A, CN111254352A, CN111793776A discloses a method for producing X65MS acid-resistant pipeline steel, and the object of the patent is to coil plates, and the patent does not relate to hot-rolled medium plates with the thickness of 15-45 mm. For a steel sheet having a certain thickness, after TMCP treatment, a medium steel sheet is liable to develop hydrogen induced cracking.
Disclosure of Invention
The application provides a pipeline steel plate with excellent hydrogen induced cracking resistance, which aims to solve the technical problem that a medium-thickness pipeline steel plate is easy to generate hydrogen induced cracks.
In a first aspect, the present application provides a pipeline steel sheet having excellent hydrogen induced cracking resistance, the chemical composition of the pipeline steel sheet including, in mass fraction: c:0.08 to 0.10 percent, si:0.01 to 0.70 percent, mn:0.8% -1.8%, P: less than or equal to 0.010 percent, S: less than or equal to 0.001 percent, al:0.025% -0.035%, nb:0.05 to 0.07 percent of Ti:0.03 to 0.05 percent of Cu:0.1 percent of 5 to 0.3 percent, and the balance of Fe and unavoidable impurity elements; the thickness of the pipeline steel plate is 15-45 mm.
Optionally, the metallographic structure of the pipeline steel plate comprises 60% -75% of polygonal ferrite, 8% -10% of pearlite and 8% -15% of acicular ferrite, and the ferrite is 16-25 μm in size.
Optionally, the average size of the ferrite is 18-20 μm.
Optionally, the hardness difference of the pipeline steel plate in the thickness direction is less than or equal to 55HV.
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 150-200 ℃;
the first cooling comprises 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; the first cooling layer and the second cooling layer are cooled to a preset temperature at a speed of 120 ℃/s-130 ℃/s respectively; and the intermediate cooling layer is cooled to the preset temperature at a speed of 30-40 ℃/s.
Optionally, in the second heating, the target temperatures of the upper surface and the lower surface of the finish rolled steel plate are 420-490 ℃, and the target temperature of the middle part of the finish rolled steel plate is 380-410 ℃.
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 adopts an economic low-carbon and low-alloy component system, has proper carbon content, can not generate segregation in the middle of the thickness of the steel plate, and has hydrogen induced cracking resistance; 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; nb can raise the recrystallization temperature of austenite, expand the temperature range of the recrystallization zone, delay the recrystallization, and effectively refine grains; the comprehensive effect improves the tissue uniformity of the medium-thickness pipeline steel plate; by combining the rolling and cooling processes, the pipeline steel plate has a uniform metallographic structure, and the problem that the medium-thickness pipeline steel plate is easy to crack due to hydrogen is avoided.
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 needed in the embodiments or 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 producing a pipeline steel sheet with excellent hydrogen induced cracking resistance 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 excellent hydrogen induced cracking resistance, wherein the chemical components of the pipeline steel plate comprise the following components in percentage by mass: c:0.08 to 0.10 percent, si:0.01 to 0.70 percent, mn:0.8% -1.8%, P: less than or equal to 0.010 percent, S: less than or equal to 0.001 percent, al:0.025% -0.035%, nb:0.05 to 0.07 percent of Ti:0.03 to 0.05 percent of Cu:0.1 percent of 5 to 0.3 percent, and the balance of Fe and unavoidable impurity elements.
In the embodiment of the application, the thickness of the pipeline steel plate is 15-45 mm.
The roles of the elements in this application are as follows:
the element C is one of means for improving strength, and if the carbon 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. Proper amounts of Nb and Ti alloy elements are added to ensure the strength, so that the content of C is controlled within the range of 0.08-0.1% by adopting ultralow carbon content.
Mn element is also extremely liable to segregate at the thickness of the steel sheet, promotes the formation of a band structure and a hard phase, and increases the content to increase the tendency of hydrogen induced cracking, deteriorating the corrosion resistance of the material. 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, mn is controlled to be in the range of 0.8 to 1.8.
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 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 the recrystallization zone, delay the recrystallization, 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 crystal grains. Thus, nb is controlled to 0.05-0.07%.
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 prevented in a welding heat affected zone, and the welding performance is improved. Therefore, ti is controlled to be within 0.03-0.05%.
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 0.15 to 0.30%.
In this application embodiment, pipeline steel sheet's thickness is 15 ~ 45mm, can reach the even effect of steel structure through the effect of first cooling, second heating, second cooling, realizes excellent hydrogen induced cracking resistance.
In the embodiment of the application, the pipeline steel plate can be X65, and X65 represents the strength level of the steel plate.
As an alternative embodiment, the metallographic structure of the pipeline steel sheet includes 60% -75% polygonal ferrite, 8% -10% pearlite and 8% -15% acicular ferrite, the ferrite having a size of 16-25 μm.
In the embodiment of the application, the metallographic structure comprises 60% -75% of polygonal ferrite, 8% -10% of pearlite and 8% -15% of acicular ferrite, and has the beneficial effects of meeting the comprehensive strengthening and toughening of the corresponding strength level, wherein the ferrite size is 16-25 mu m, and the beneficial effects of reducing the internal stress of the steel plate are achieved.
As an alternative embodiment, the ferrite has an average size of 18-20 μm.
In the embodiment of the application, the average size of the ferrite is 18-20 mu m, and the ferrite has the beneficial effects of excellent comprehensive mechanical properties and hydrogen induced cracking resistance, which are matched with pearlite and acicular ferrite.
As an alternative embodiment, the hardness difference of the pipeline steel plate in the thickness direction is less than or equal to 55HV.
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 55HV, 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 the position of the pipeline steel plate which is about 10 cm to 24cm away from the upper surface and the lower surface, the hardness of the middle part of the pipeline steel plate is less than or equal to 270HV, and the pipeline steel plate has the beneficial effects of avoiding the excessive internal stress of the steel plate and reducing the occurrence of cracks; 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 40HV, and the composition system has the beneficial effect of tissue uniformity along the thickness direction.
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 producing 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;
s2, performing first heating, rough rolling and finish rolling on the plate blank to obtain a finish-rolled steel plate;
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 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 ℃.
As an alternative embodiment, the end point temperature of the first cooling is 150-200 ℃;
the first cooling comprises 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; the first cooling layer and the second cooling layer are cooled to a preset temperature at a speed of 120 ℃/s-130 ℃/s respectively; and the intermediate cooling layer is cooled to the preset temperature at a speed of 30-40 ℃/s.
In this embodiment, the preset temperature may be 560 ℃.
As an alternative embodiment, in the second heating, the target temperature of the upper and lower surfaces of the finish rolled steel sheet is 420 to 490 ℃ and the target temperature of the middle portion of the finish rolled steel sheet is 380 to 410 ℃.
As an alternative embodiment, the second cooling includes air cooling to room temperature.
In the embodiment of the application, the reason for controlling the target temperature of the upper surface and the lower surface of the finish rolling steel plate to be 420-490 ℃ is the proportion of each phase in the refined control structure, the reason for controlling the target temperature of the middle part of the finish rolling steel plate to be 380-410 ℃ is the refined control structure, and the uniformity of the finish rolling steel plate and the upper surface and the lower surface structure is kept to a certain degree.
In this embodiment of the present application, the method for manufacturing a pipeline steel plate may sequentially perform first heating, rough rolling, finish rolling, first cooling, second heating, and second cooling on the slab, and the second cooling may be air cooling.
In the embodiment of the application, the rolling and the first cooling control the structure 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.
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 of the chemical composition (balance of Fe and unavoidable impurities) as in Table 1 were heated to 1100 to 1200 ℃, and then subjected to rough rolling, finish rolling and water cooling to obtain steel sheets of 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 | 26 | 7 | 6 |
As can be seen from Table 4, the yield strength of the example group is greater than 470MPa, the tensile strength is greater than 560MPa, the Charpy impact energy at-10 ℃ is greater than 460J, and the hardness difference of the pipeline steel plates in the thickness direction is less than or equal to 55HV; the hardness of the middle part of the pipeline steel plate in the thickness direction is less than or equal to 270HV, and the difference value of the hardness of the soft phase structure of the middle part and the hardness of the hard phase structure of the middle part is less than or equal to 40HV, so that the steel plate has excellent performance, uniform structure and difficult occurrence of hydrogen induced cracking; in comparative example 1, the yield strength was lower than 400MPa, the tensile strength was lower than 500MPa, and the hardness difference in the thickness direction of the steel sheet for pipeline was 60HV; the hardness of the middle part of the pipeline steel plate in the thickness direction is 289HV, the hardness difference between the soft phase structure of the middle part and the hard phase structure of the middle part is as high as 58HV, which indicates that the steel plate has lower strength and even and poorer structure; as can be seen from Table 5, the pipeline steel plate has excellent cracking resistance, while the comparative example 1 has poor hydrogen induced cracking resistance, and is difficult to meet the practical 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 of the present application has different types and proportions of metallographic structures from the steel plate of comparative example 1, and has different mechanical properties and cracking resistance.
It should be noted that 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 (9)
1. A pipeline steel sheet having excellent hydrogen induced cracking resistance, characterized in that the chemical composition of the pipeline steel sheet comprises, in mass fraction: c is 0.08% -0.10%, si:0.01% -0.70%, mn:0.8% -1.8%, P: less than or equal to 0.010 percent, S: less than or equal to 0.001 percent, al:0.025% -0.035%, nb:0.05% -0.07%, ti:0.03% -0.05%, cu:0.15% -0.3%, and the balance being Fe and unavoidable impurity elements; the metallographic structure of the pipeline steel plate comprises 60% -75% of polygonal ferrite, 8% -10% of pearlite and 8% -15% of acicular ferrite, and the size of the ferrite is 16-25 microns.
2. The line steel sheet according to claim 1, wherein the average size of the ferrite is 18-20 μm.
3. The line steel sheet according to claim 1, wherein the hardness difference in the thickness direction of the line steel sheet is not more than 55HV.
4. A method for producing a pipeline steel sheet as claimed in any one of claims 1 to 3, 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.
5. The method according to claim 4, wherein the first heating is performed at a temperature of 1100-1200 ℃ for a time of 60-75 min.
6. The method according to claim 4, wherein 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 ℃.
7. The method of claim 4, wherein the first cooling has an endpoint temperature of 150-200 ℃;
the first cooling comprises 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; the first cooling layer and the second cooling layer are cooled to a preset temperature at the speed of 120 ℃/s-130 ℃/s respectively; and cooling the intermediate cooling layer to the preset temperature at a speed of 30-40 ℃/s.
8. The method according to claim 4, wherein in the second heating, the target temperature of the upper surface and the lower surface of the finish rolled steel sheet is 420 to 490 ℃ and the target temperature of the middle portion of the finish rolled steel sheet is 380 to 410 ℃.
9. The method of claim 4, wherein the second cooling comprises air cooling to room temperature.
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Citations (14)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| GB1491729A (en) * | 1973-12-28 | 1977-11-16 | Sumitomo Metal Ind | Steel pipelines which are resistant to hydrogen-induced cracking |
| JP2005060820A (en) * | 2003-07-31 | 2005-03-10 | Jfe Steel Kk | High strength steel sheet for line pipe excellent in anti-hic (hydrogen induced cracking) characteristic and its manufacturing method |
| JP2005264217A (en) * | 2004-03-17 | 2005-09-29 | Jfe Steel Kk | Thick hot rolled steel plate having excellent hic resistance and its production method |
| JP2006111928A (en) * | 2004-10-15 | 2006-04-27 | Sumitomo Metal Ind Ltd | Thick steel plate for line pipe and its production method |
| CN101054649A (en) * | 2007-03-29 | 2007-10-17 | 攀钢集团成都钢铁有限责任公司 | Sulfur erosion resisting steel and smelting method thereof |
| CN102286690A (en) * | 2011-08-30 | 2011-12-21 | 南京钢铁股份有限公司 | Pipeline steel plate capable of resisting hydrogen-induced cracking and production method thereof |
| CN102828116A (en) * | 2011-06-14 | 2012-12-19 | 鞍钢股份有限公司 | TMCP (thermal mechanical control processing) process-based surface-layer ultrafine-grain high-strength steel plate and manufacturing method thereof |
| CN103866187A (en) * | 2014-03-24 | 2014-06-18 | 济钢集团有限公司 | Steel plate for 500MPa-level pressure container for resisting sulfide stress corrosion cracking and production method thereof |
| JP2014189808A (en) * | 2013-03-26 | 2014-10-06 | Kobe Steel Ltd | Low yield ratio-type high strength steel sheet excellent in hydrogen induced cracking resistance and bendability |
| CN105220069A (en) * | 2015-10-14 | 2016-01-06 | 南京钢铁股份有限公司 | A kind of nearly table Ultra-fine Grained super low carbon microalloy high strength steel Wide and Thick Slab and method for making thereof |
| CN105695863A (en) * | 2016-02-04 | 2016-06-22 | 首钢总公司 | Hot-rolled coiled plate for natural gas delivery pipeline and manufacturing method thereof |
| 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 |
| CN110306117A (en) * | 2019-08-02 | 2019-10-08 | 武汉钢铁集团鄂城钢铁有限责任公司 | A kind of high uniformity super thick structural steel plate and its manufacturing method |
| CN113234994A (en) * | 2021-04-14 | 2021-08-10 | 马鞍山钢铁股份有限公司 | Hot-rolled high-strength weather-resistant steel plate with yield strength of 600MPa and production method thereof |
-
2022
- 2022-04-27 CN CN202210455726.9A patent/CN114921721B/en active Active
Patent Citations (14)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| GB1491729A (en) * | 1973-12-28 | 1977-11-16 | Sumitomo Metal Ind | Steel pipelines which are resistant to hydrogen-induced cracking |
| JP2005060820A (en) * | 2003-07-31 | 2005-03-10 | Jfe Steel Kk | High strength steel sheet for line pipe excellent in anti-hic (hydrogen induced cracking) characteristic and its manufacturing method |
| JP2005264217A (en) * | 2004-03-17 | 2005-09-29 | Jfe Steel Kk | Thick hot rolled steel plate having excellent hic resistance and its production method |
| JP2006111928A (en) * | 2004-10-15 | 2006-04-27 | Sumitomo Metal Ind Ltd | Thick steel plate for line pipe and its production method |
| CN101054649A (en) * | 2007-03-29 | 2007-10-17 | 攀钢集团成都钢铁有限责任公司 | Sulfur erosion resisting steel and smelting method thereof |
| CN102828116A (en) * | 2011-06-14 | 2012-12-19 | 鞍钢股份有限公司 | TMCP (thermal mechanical control processing) process-based surface-layer ultrafine-grain high-strength steel plate and manufacturing method thereof |
| CN102286690A (en) * | 2011-08-30 | 2011-12-21 | 南京钢铁股份有限公司 | Pipeline steel plate capable of resisting hydrogen-induced cracking and production method thereof |
| JP2014189808A (en) * | 2013-03-26 | 2014-10-06 | Kobe Steel Ltd | Low yield ratio-type high strength steel sheet excellent in hydrogen induced cracking resistance and bendability |
| CN103866187A (en) * | 2014-03-24 | 2014-06-18 | 济钢集团有限公司 | Steel plate for 500MPa-level pressure container for resisting sulfide stress corrosion cracking and production method thereof |
| CN105220069A (en) * | 2015-10-14 | 2016-01-06 | 南京钢铁股份有限公司 | A kind of nearly table Ultra-fine Grained super low carbon microalloy high strength steel Wide and Thick Slab and method for making thereof |
| CN105695863A (en) * | 2016-02-04 | 2016-06-22 | 首钢总公司 | Hot-rolled coiled plate for natural gas delivery pipeline and manufacturing method thereof |
| 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 |
| CN110306117A (en) * | 2019-08-02 | 2019-10-08 | 武汉钢铁集团鄂城钢铁有限责任公司 | A kind of high uniformity super thick structural steel plate and its manufacturing method |
| CN113234994A (en) * | 2021-04-14 | 2021-08-10 | 马鞍山钢铁股份有限公司 | Hot-rolled high-strength weather-resistant steel plate with yield strength of 600MPa and production method thereof |
Non-Patent Citations (1)
| Title |
|---|
| 高强度管线钢的抗氢致裂纹性能;李云涛等;《钢铁研究学报》;第20卷(第12期);全文 * |
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