CN112430710A - Preparation method of high-strength and high-toughness heterogeneous tissue drill collar material and drill collar material - Google Patents
Preparation method of high-strength and high-toughness heterogeneous tissue drill collar material and drill collar material Download PDFInfo
- Publication number
- CN112430710A CN112430710A CN202011211849.5A CN202011211849A CN112430710A CN 112430710 A CN112430710 A CN 112430710A CN 202011211849 A CN202011211849 A CN 202011211849A CN 112430710 A CN112430710 A CN 112430710A
- Authority
- CN
- China
- Prior art keywords
- drill collar
- collar material
- treatment
- strength
- heterogeneous
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Pending
Links
- 239000000463 material Substances 0.000 title claims abstract description 66
- 238000002360 preparation method Methods 0.000 title claims abstract description 20
- 229910001220 stainless steel Inorganic materials 0.000 claims abstract description 56
- 239000010935 stainless steel Substances 0.000 claims abstract description 55
- 239000013078 crystal Substances 0.000 claims abstract description 46
- 238000007709 nanocrystallization Methods 0.000 claims abstract description 44
- 238000005097 cold rolling Methods 0.000 claims abstract description 40
- 238000000137 annealing Methods 0.000 claims abstract description 38
- 238000000034 method Methods 0.000 claims abstract description 34
- 238000001953 recrystallisation Methods 0.000 claims abstract description 31
- 238000011282 treatment Methods 0.000 claims description 94
- 239000000243 solution Substances 0.000 claims description 25
- 239000002159 nanocrystal Substances 0.000 claims description 23
- 230000009467 reduction Effects 0.000 claims description 15
- 239000006104 solid solution Substances 0.000 claims description 14
- 238000005096 rolling process Methods 0.000 claims description 9
- 229910001566 austenite Inorganic materials 0.000 claims description 8
- 238000004381 surface treatment Methods 0.000 claims description 5
- 238000000227 grinding Methods 0.000 claims description 4
- 238000005422 blasting Methods 0.000 claims description 3
- 238000004220 aggregation Methods 0.000 claims 1
- 230000002776 aggregation Effects 0.000 claims 1
- 238000005260 corrosion Methods 0.000 abstract description 32
- 230000007797 corrosion Effects 0.000 abstract description 31
- 230000002787 reinforcement Effects 0.000 abstract description 2
- 239000010410 layer Substances 0.000 description 18
- FAPWRFPIFSIZLT-UHFFFAOYSA-M Sodium chloride Chemical compound [Na+].[Cl-] FAPWRFPIFSIZLT-UHFFFAOYSA-M 0.000 description 8
- 238000001816 cooling Methods 0.000 description 8
- 238000005553 drilling Methods 0.000 description 7
- 238000010438 heat treatment Methods 0.000 description 7
- 229910000963 austenitic stainless steel Inorganic materials 0.000 description 6
- 238000004321 preservation Methods 0.000 description 6
- 230000008569 process Effects 0.000 description 6
- 239000002344 surface layer Substances 0.000 description 6
- 238000012545 processing Methods 0.000 description 5
- 230000002829 reductive effect Effects 0.000 description 5
- 238000005728 strengthening Methods 0.000 description 5
- 230000003247 decreasing effect Effects 0.000 description 4
- 238000011161 development Methods 0.000 description 4
- 239000012535 impurity Substances 0.000 description 4
- 229910000734 martensite Inorganic materials 0.000 description 4
- 239000011780 sodium chloride Substances 0.000 description 4
- 238000012360 testing method Methods 0.000 description 4
- 229910000831 Steel Inorganic materials 0.000 description 3
- 229910052804 chromium Inorganic materials 0.000 description 3
- 230000000052 comparative effect Effects 0.000 description 3
- 229910052750 molybdenum Inorganic materials 0.000 description 3
- 229910052759 nickel Inorganic materials 0.000 description 3
- 239000010959 steel Substances 0.000 description 3
- 238000005299 abrasion Methods 0.000 description 2
- 230000001133 acceleration Effects 0.000 description 2
- 230000008859 change Effects 0.000 description 2
- 230000007423 decrease Effects 0.000 description 2
- 238000009826 distribution Methods 0.000 description 2
- 238000005516 engineering process Methods 0.000 description 2
- 239000000203 mixture Substances 0.000 description 2
- 230000004048 modification Effects 0.000 description 2
- 238000012986 modification Methods 0.000 description 2
- 230000035945 sensitivity Effects 0.000 description 2
- 238000005482 strain hardening Methods 0.000 description 2
- 230000001360 synchronised effect Effects 0.000 description 2
- 230000009466 transformation Effects 0.000 description 2
- 102100030569 Nuclear receptor corepressor 2 Human genes 0.000 description 1
- 101710153660 Nuclear receptor corepressor 2 Proteins 0.000 description 1
- 230000006978 adaptation Effects 0.000 description 1
- 230000002411 adverse Effects 0.000 description 1
- 229910045601 alloy Inorganic materials 0.000 description 1
- 239000000956 alloy Substances 0.000 description 1
- 238000005452 bending Methods 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 239000010960 cold rolled steel Substances 0.000 description 1
- 230000006835 compression Effects 0.000 description 1
- 238000007906 compression Methods 0.000 description 1
- 238000010276 construction Methods 0.000 description 1
- 238000005520 cutting process Methods 0.000 description 1
- 230000000694 effects Effects 0.000 description 1
- 238000006056 electrooxidation reaction Methods 0.000 description 1
- 230000003628 erosive effect Effects 0.000 description 1
- 230000002349 favourable effect Effects 0.000 description 1
- 230000006870 function Effects 0.000 description 1
- 238000005098 hot rolling Methods 0.000 description 1
- 230000006872 improvement Effects 0.000 description 1
- 238000012994 industrial processing Methods 0.000 description 1
- 238000009776 industrial production Methods 0.000 description 1
- 239000011229 interlayer Substances 0.000 description 1
- 230000002427 irreversible effect Effects 0.000 description 1
- 230000000670 limiting effect Effects 0.000 description 1
- 238000004519 manufacturing process Methods 0.000 description 1
- 239000011159 matrix material Substances 0.000 description 1
- 238000005259 measurement Methods 0.000 description 1
- 238000003701 mechanical milling Methods 0.000 description 1
- 229910052751 metal Inorganic materials 0.000 description 1
- 239000002184 metal Substances 0.000 description 1
- 239000007769 metal material Substances 0.000 description 1
- 230000003647 oxidation Effects 0.000 description 1
- 238000007254 oxidation reaction Methods 0.000 description 1
- 230000036961 partial effect Effects 0.000 description 1
- 239000012466 permeate Substances 0.000 description 1
- 238000005498 polishing Methods 0.000 description 1
- 238000003825 pressing Methods 0.000 description 1
- 238000011160 research Methods 0.000 description 1
- 239000011435 rock Substances 0.000 description 1
- 238000005204 segregation Methods 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
- 239000000758 substrate Substances 0.000 description 1
- 238000010998 test method Methods 0.000 description 1
- 238000009210 therapy by ultrasound Methods 0.000 description 1
Classifications
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/26—Methods of annealing
-
- 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
- C21D10/00—Modifying the physical properties by methods other than heat treatment or deformation
-
- 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
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
-
- 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
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/005—Heat treatment of ferrous alloys containing Mn
-
- 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
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/008—Heat treatment of ferrous alloys containing Si
-
- 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
- C21D8/0236—Cold 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
- 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
- C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
-
- 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
- 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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
-
- 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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
-
- E—FIXED CONSTRUCTIONS
- E21—EARTH OR ROCK DRILLING; MINING
- E21B—EARTH OR ROCK DRILLING; OBTAINING OIL, GAS, WATER, SOLUBLE OR MELTABLE MATERIALS OR A SLURRY OF MINERALS FROM WELLS
- E21B17/00—Drilling rods or pipes; Flexible drill strings; Kellies; Drill collars; Sucker rods; Cables; Casings; Tubings
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Crystallography & Structural Chemistry (AREA)
- Thermal Sciences (AREA)
- Life Sciences & Earth Sciences (AREA)
- Geology (AREA)
- Mining & Mineral Resources (AREA)
- Environmental & Geological Engineering (AREA)
- Fluid Mechanics (AREA)
- General Life Sciences & Earth Sciences (AREA)
- Geochemistry & Mineralogy (AREA)
- Heat Treatment Of Steel (AREA)
Abstract
The invention relates to the field of drill collar material reinforcement, in particular to a preparation method of a high-strength high-toughness heterogeneous structure drill collar material and the drill collar material. The invention adopts the method of combining cold rolling, incomplete recrystallization annealing and surface nanocrystallization to prepare the heterogeneous layered structure stainless steel with the surface superfine nanocrystalline layer, nanometer twin crystal, micron recrystallization and residual elongated deformation coarse crystal phase, the surface superfine nanocrystalline layer can effectively improve the corrosion resistance and the surface smoothness of the stainless steel, the hard nanometer twin crystal can effectively improve the strength of the stainless steel, the soft micron recrystallization and residual elongated deformation coarse crystal ensure the plasticity of the material, a large number of soft and hard interfaces can effectively coordinate the deformation, the strength and the plasticity of the material can be further improved through the back stress form, and the mechanical property requirement under the harsh condition can be met, so that the stainless steel has high mechanical property and good corrosion resistance.
Description
Technical Field
The invention relates to the field of drill collar material reinforcement, in particular to a preparation method of a high-strength high-toughness heterogeneous structure drill collar material and the drill collar material.
Background
With the strategic demand of exploration and development of oil and gas resources, the drilling technology of deep wells, ultra-deep wells and ultra-deep wells is the guarantee for realizing exploration and development of oil and gas resources in deep strata, and the exploration and development of deep ultra-deep wells provide higher requirements for the service performance of materials for drilling machines, such as greater challenges for the performances of abrasion (caused by different rock stratum characteristics), fatigue fracture (torsion, compression, centrifugal force, dynamic load and the like), corrosion (stress corrosion fracture, intergranular corrosion, uniform corrosion, electrochemical corrosion, wind corrosion, erosion, crack corrosion and the like) and the like of the drilling machines. The drill collar is an important component of a drill string in the process of drilling deep ultra-deep oil and gas and is used for providing the bit pressure required by a drill bit for cutting a stratum and preventing well deviation, wherein the non-magnetic drill collar ensures the accuracy of the measurement result of a logging instrument (utilizing the magnetic principle) and ensures that a well track meets the requirement. The method is long in service for directional wells, horizontal wells, extended reach wells and vertical wells with high requirements. Wherein, alternating bending stress, stress corrosion and abrasion are main factors causing the failure and the damage of the drill collar material. According to statistics, drilling tool accidents happen hundreds of times every year in China, wherein the drill collar is large in failure occupation ratio, and the economic loss reaches hundreds of millions of yuan. Drill collar fracture failure often occurs in the construction of ultra-deep complex geological environment, and major accidents are directly caused to cause major economic loss.
Stainless steels, such as 316L austenitic stainless steel, are widely used in drill collar production due to their excellent oxidation and corrosion resistance, as well as their good work hardening and formability. However, the yield strength of the coarse-crystalline austenitic stainless steel is low, and is generally only 100-300 MPa at normal temperature, so that the application of the coarse-crystalline austenitic stainless steel in the ultra-deep drilling technology is severely restricted. Deep ultra-deep oil and gas exploration and development have higher requirements on the service performance of materials for drilling machines and tools and the strong plasticity matching performance of stainless steel, so that the rapid preparation of large batches of stainless steel with good strong plasticity matching is very important. However, the mechanical property and the corrosion resistance of the traditional processing strengthening cannot be effectively enhanced, and the balance between the mechanical property and the corrosion resistance is achieved, so that the method which is more economical and effective and can meet the industrial processing requirement is particularly important to find.
Disclosure of Invention
In order to solve the above problems, a first aspect of the present invention provides a method for preparing a high-strength high-toughness heterogeneous tissue drill collar material, comprising:
the heterogeneous structure drill collar material is obtained by sequentially carrying out solid solution treatment, cold rolling treatment, incomplete recrystallization annealing treatment and surface nanocrystallization treatment on stainless steel.
In a preferable technical scheme of the invention, in the solution treatment, the stainless steel is kept at 850-1150 ℃ for 20-600 min, and is air-cooled to room temperature to obtain an austenite structure, wherein the average grain size of the austenite structure is 30-130 μm.
As a preferable technical scheme, in the cold rolling treatment, the total cold rolling reduction is 60-85%, and the cold rolling speed is less than or equal to 12 m/min.
As a preferable technical scheme, in the incomplete recrystallization annealing treatment, the annealing temperature is 700-900 ℃, and the annealing time is 5-60 min.
As a preferable technical scheme of the invention, after the surface nanocrystallization treatment, a surface superfine nanocrystalline layer with the thickness of 10-45 mu m is formed.
As a preferable technical scheme, in the surface nanocrystallization treatment, the surface nanocrystallization treatment time is 30-360 min, and the surface nanocrystallization times are not less than 36690 times/m2。
As a preferred embodiment of the present invention, the surface nanocrystallization treatment is one selected from the group consisting of surface mechanical polishing treatment, surface mechanical grinding treatment, surface mechanical rolling treatment, ultrasonic impact surface treatment, and rotational acceleration peening treatment.
As a preferable technical scheme, the structure of the heterogeneous tissue drill collar material is a heterogeneous layered structure, and the heterogeneous layered structure comprises recrystallized grains aggregated in a strip shape, refined ultrafine grains, nano-crystals, nano-twin crystals and elongated deformed coarse crystals.
As a preferable technical scheme of the invention, the volume fraction of the ribbon-shaped aggregated recrystallization is generally 10-60%, the average grain size is 1-8 μm, the volume fraction of the nano twin crystal is 5-20%, the volume fraction of the nano crystal is 15-55%, and the volume fraction of the elongated deformed coarse crystal is 5-15%.
The invention provides a heterogeneous tissue drill collar material in a second aspect, which is prepared by the preparation method of the high-strength and high-toughness heterogeneous tissue drill collar material.
Compared with the prior art, the invention has the following beneficial effects:
1) the invention adopts a method combining cold rolling, incomplete recrystallization annealing and surface nanocrystallization to prepare the heterogeneous layered structure stainless steel with surface superfine nanocrystalline layers, nanometer twin crystals, micron recrystallization and mixed residual elongated deformation coarse crystalline phases.
2) The surface superfine nanocrystalline layer in the heterogeneous layered structure can effectively improve the corrosion resistance of the heterogeneous layered structure, the surface smoothness of stainless steel, particularly 316L stainless steel, can be effectively improved by hard nanometer twin crystals, the strength of the stainless steel, particularly 316L stainless steel, can be effectively improved by soft micron recrystallization and residual elongated deformation coarse crystals, the plasticity of the material is ensured, meanwhile, a large number of soft and hard interfaces can be effectively coordinated and deformed, the strength and the plasticity of the material are further improved by a back stress form, the mechanical property of the material is improved by 2-3 times compared with that of the stainless steel before treatment, and the mechanical property requirement under severe conditions can be met.
3) The stainless steel is subjected to solid solution and cold rolling treatment to obtain nanocrystalline, nano twin crystal and ultrafine crystal waiting cold rolled structures, then annealing is carried out, partial ultrafine crystal, nano twin crystal and the like are converted into recrystallized grains to obtain heterogeneous layered structures, finally surface nanocrystallization treatment is carried out, a surface ultrafine nanocrystalline layer with a certain thickness is formed on the surface of the cold rolled structures, grains are further refined, a layered structure with a certain thickness and proper grain length are obtained, and the stainless steel has high strength and high toughness mechanical properties and good corrosion resistance.
4) The preparation method provided by the invention has simple conditions and easy operation, and can be used for large-scale industrial production.
Detailed Description
The disclosure may be understood more readily by reference to the following detailed description of preferred embodiments of the invention and the examples included therein. Unless defined otherwise, all technical and scientific terms used herein have the same meaning as commonly understood by one of ordinary skill in the art to which this invention belongs. In case of conflict, the present specification, including definitions, will control.
The term "prepared from …" as used herein is synonymous with "comprising". The terms "comprises," "comprising," "includes," "including," "has," "having," "contains," "containing," or any other variation thereof, as used herein, are intended to cover a non-exclusive inclusion. For example, a composition, process, method, article, or apparatus that comprises a list of elements is not necessarily limited to only those elements but may include other elements not expressly listed or inherent to such composition, process, method, article, or apparatus.
The conjunction "consisting of …" excludes any unspecified elements, steps or components. If used in a claim, the phrase is intended to claim as closed, meaning that it does not contain materials other than those described, except for the conventional impurities associated therewith. When the phrase "consisting of …" appears in a clause of the subject matter of the claims rather than immediately after the subject matter, it defines only the elements described in the clause; other elements are not excluded from the claims as a whole.
When an amount, concentration, or other value or parameter is expressed as a range, preferred range, or as a range of upper preferable values and lower preferable values, this is to be understood as specifically disclosing all ranges formed from any pair of any upper range limit or preferred value and any lower range limit or preferred value, regardless of whether ranges are separately disclosed. For example, when a range of "1 to 5" is disclosed, the described range should be interpreted to include the ranges "1 to 4", "1 to 3", "1 to 2 and 4 to 5", "1 to 3 and 5", and the like. When a range of values is described herein, unless otherwise stated, the range is intended to include the endpoints thereof and all integers and fractions within the range.
The singular forms "a", "an" and "the" include plural referents unless the context clearly dictates otherwise. "optional" or "any" means that the subsequently described event or events may or may not occur, and that the description includes instances where the event occurs and instances where it does not.
Approximating language, as used herein throughout the specification and claims, is intended to modify a quantity, such that the invention is not limited to the specific quantity, but includes portions that are literally received for modification without substantial change in the basic function to which the invention is related. Accordingly, the use of "about" to modify a numerical value means that the invention is not limited to the precise value. In some instances, the approximating language may correspond to the precision of an instrument for measuring the value. In the present description and claims, range limitations may be combined and/or interchanged, including all sub-ranges contained therein if not otherwise stated.
In addition, the indefinite articles "a" and "an" preceding an element or component of the invention are not intended to limit the number requirement (i.e., the number of occurrences) of the element or component. Thus, "a" or "an" should be read to include one or at least one, and the singular form of an element or component also includes the plural unless the stated number clearly indicates that the singular form is intended.
The present invention is illustrated by the following specific embodiments, but is not limited to the specific examples given below.
The invention provides a preparation method of a high-strength and high-toughness heterogeneous tissue drill collar material, which comprises the following steps:
the heterogeneous structure drill collar material is obtained by sequentially carrying out solid solution treatment, cold rolling treatment, incomplete recrystallization annealing treatment and surface nanocrystallization treatment on stainless steel.
The invention researches stainless steel, particularly austenitic stainless steel to improve mechanical and anti-corrosion performances, wherein the austenitic stainless steel refers to stainless steel with an austenitic structure at normal temperature. The austenitic stainless steel of the present invention may be, for example, 316L, 904L, 317LMN, 254SMO, 654SMO, preferably 316L. In a preferred embodiment, the stainless steel of the present invention comprises the following components by weight percent: less than or equal to 0.03 wt% of C, less than or equal to 1.0 wt% of Si, less than or equal to 2.0 wt% of Mn, less than or equal to 0.045 wt% of P, less than or equal to 0.03 wt% of S, Ni: 10.0-14.0 wt%, Cr: 16.0 to 18.0 wt%, Mo: 2.0 to 3.0 wt%, and the balance Fe and inevitable impurities.
Solution treatment
The solution treatment (solution treatment) refers to a heat treatment process for heating the alloy to a high-temperature single-phase zone and keeping the temperature constant, so that the excess phase is fully dissolved in the solid solution and then is rapidly cooled to obtain a supersaturated solid solution, and finally a proper grain size is obtained. In one embodiment, in the solution treatment, the stainless steel is kept at 850-1150 ℃ for 20-600 min, and is air-cooled to room temperature to obtain an austenite structure; in one embodiment, in the solution treatment, after the temperature is raised to 850-1150 ℃, stainless steel is placed into the solution for heat preservation for 20-600 min, and the solution is cooled to room temperature.
The applicant finds that the proper grain size can be obtained by controlling the solid solution temperature and time, the grain size increases along with the increase of the temperature and time, the applicant finds that the proper grain size is obtained when the solid solution temperature is 850-1150 ℃, and the uniformity of the grains increases along with the increase of the temperature, but the applicant finds that when the temperature is higher than 1150 ℃, the solid solution effect of carbide is enhanced, the grains become coarse, the mechanical property is reduced, and the subsequent processing is not facilitated. Preferably, in the solid solution treatment, the solid solution temperature is 850-1150 ℃, and the heat preservation time is 20-600 min; in a preferred embodiment, in the solid solution treatment, the solid solution temperature is 850-1150 ℃, and the heat preservation time is 100-600 min; in a preferred embodiment, in the solution treatment of the present invention, the solution temperature is 850 to 1150 ℃ and the holding time is 200 to 500 min.
The applicant finds that the grain size can be controlled within 30-130 mu m after air cooling by controlling the solid solution temperature and time, so that the transformation of a martensite structure in subsequent cold rolling and the generation of nano-crystal, ultra-fine crystal and nano-twin crystal are facilitated. More preferably, the average grain size of the austenitic structure is 30-130 μm; in one embodiment, the austenitic structure of the present invention has an average grain size of 30 to 100 μm; in one embodiment, the austenitic structure of the present invention has an average grain size of 30 to 80 μm.
The average grain size represents the size of the grains, and the present invention does not further limit the specific test method for the average grain size, and may be exemplified by XRD.
Cold rolling treatment
Cold rolling is the further rolling of the material to a target thickness at room temperature. Compared with hot rolling, the cold rolling has more accurate thickness, smooth and beautiful surface and various excellent mechanical properties, especially processing property. However, since a cold rolled raw coil is relatively brittle and hard and is not suitable for working, the cold rolled steel sheet is generally required to be subjected to a step of annealing or the like, and the present invention does not limit the apparatus for cold rolling treatment, and there may be mentioned a cold rolling mill such as a medium-sized synchronous rolling mill. In one embodiment, in the cold rolling treatment according to the present invention, the cold rolling treatment is performed on the austenite structure at room temperature to obtain a cold rolled sheet.
Preferably, the thickness of the stainless steel is 5-35 mm, and the thickness of the cold-rolled plate is 0.3-6 mm.
The applicant found that when the cold rolling reduction and the cold rolling speed are controlled, it is advantageous to promote transformation of austenite to martensite, as the reduction and the cold rolling speed are increased, the austenite grain assembly is transformed into martensite grains, the number of shear bands is reduced, when the reduction is 60%, the structure is mainly composed of martensite, refined ultra-fine grains, nano-crystals, nano-twins are generated, and finally a band-shaped cold rolled structure is formed, and as the reduction is increased, the hardness, yield strength and tensile strength after cold rolling are increased, but the applicant found that when the reduction is more than 85%, the elongation is decreased. More preferably, in the cold rolling treatment, the total cold rolling reduction amount is 60-85%, and the cold rolling speed is less than or equal to 12 m/min.
The total cold rolling pressing amount is the reduction of the height of the rolled piece after cold rolling.
The cold rolling speed is the reduction in height per minute after cold rolling.
Further preferably, in the cold rolling treatment of the present invention, the reduction per pass is 0.04 to 0.1 mm.
Annealing treatment for incomplete recrystallization
Recrystallization annealing (recrystallization annealing) is a process of heating a workpiece subjected to cold deformation processing to a temperature higher than the recrystallization temperature, preserving heat for a certain time, and then cooling to recrystallize the workpiece, thereby eliminating work hardening. The annealing only needs to set the highest heating temperature and the heat preservation time generally, the heating and cooling speed can not be considered, and the annealing is characterized in that the structure and the performance are in one-way irreversible change. In one embodiment, in the annealing treatment for incomplete recrystallization according to the present invention, the stainless steel after the solution treatment, the cold rolling treatment, and the surface nanocrystallization treatment is annealed and then air-cooled to room temperature.
Annealing the 316L stainless steel at 700-900 ℃ for 5-60 min, then rapidly cooling to room temperature, in the heat preservation process, preferentially recrystallizing the severely deformed region in the original cold deformation structure to form banded recrystallization segregation, and forming a heterogeneous layered structure together with the nano twin crystal, the residual ultrafine crystal/nano crystal and the residual elongated deformed coarse crystal. The applicant finds that more recrystallized grains are generated by the interlamellar nano-crystal, twin crystal, superfine crystal and the like through annealing treatment, the volume fraction and the average grain size of the recrystallization are increased, the volume fraction and the average grain size of the recrystallization can be controlled to be proper when the annealing temperature and the annealing time are set, and the nano-twin crystal beam, the nano-crystal, the superfine crystal and the like exist among the recrystallization, so that the mechanical property is improved, and the corrosion resistance is improved. The applicant finds that when the annealing temperature is too high or the annealing time is too long, the integral number of the recrystallized body is too large, the interlayer is excessively fused, the structure of the surface nanocrystalline layer can be influenced by the excessively high annealing temperature and time, the mechanical property and the corrosion property are adversely affected, and when the annealing temperature and time are small, the nanocrystalline layer cannot completely permeate into the tissue, and the mechanical property is also affected. Preferably, in the incomplete recrystallization annealing treatment, the annealing temperature is 700-900 ℃, and the annealing time is 5-60 min; further, in the incomplete recrystallization annealing treatment, the annealing temperature is 700-850 ℃, and the annealing time is 10-30 min.
Surface nanocrystallization
The surface nanocrystallization is to refine surface crystal grains of the material to a nanometer level by various physical or chemical methods to prepare a surface superfine nanocrystalline layer, and a matrix still keeps the original state, so that the surface properties of the material, such as fatigue strength, corrosion resistance, wear resistance and the like, are improved and enhanced. The applicant has found that it is necessary to control the depth of the nano-surface layer after the surface nanocrystallization, and thus the thickness of each layer of the final heterogeneous layered structure, and found that the corrosion performance is related to the thickness of each layer in the final resultant structure, while the stress performance is related to the thickness of each layer and the size of crystal grains, such as length, and both affect each other, even the opposite, and when the depth of the nano-surface layer is not proper, the distribution and proportion of the formed ultra-fine crystals, nano-twin crystals, and the like also affect the formation and distribution of the final heterogeneous layered structure, so that the balance between the corrosion resistance and the mechanical properties cannot be achieved. In one embodiment, the surface of the substrate is processed into a nano-crystalline surface with a thickness of 10-45 μm.
The applicant found that as the surface nanocrystallization time increases, the crystal grain size of the surface layer decreases, the depth of the surface ultrafine nanocrystal layer increases, the surface ultrafine nanocrystal layer and the surface participate in the generation of pressure, so that the corrosion sensitivity decreases, but the applicant found that as the treatment time continues to increase, the nanocrystals slightly recover due to the increase of the treatment temperature, the crystal grain size increases, and twin crystals, slip steps and the like cause the increase of the corrosion sensitivity, which is not favorable for the corrosion resistance. Preferably, in the surface nanocrystallization treatment, the surface nanocrystallization treatment time is 30-360 min, and the surface nanocrystallization times are not less than 36690 times/m2. Furthermore, in the surface nanocrystallization treatment, the surface nanocrystallization treatment time is 80-240 min, and the surface nanocrystallization times are not less than 36690 times/m2。
The current methods for surface nanocrystallization include mechanical or ultrasonic treatments, such as Surface Mechanical Grinding (SMGT), surface mechanical milling (SMRT), surface mechanical rolling (USSP), ultrasonic impact surface treatment, and rotational accelerated shot blasting (RASP). Ultrasonic Impact (UIT) surface nanocrystallization is a novel method for conveniently, quickly and inexpensively carrying out large-scale surface nanocrystallization processing on metal mechanical parts by utilizing ultrasonic energy, and a nanocrystal structure can be obtained on the surfaces of various metal materials by ultrasonic impact to form a gradient structure with the surface being nanocrystal and the size of crystal grains gradually increasing along the thickness direction. More preferably, the surface nanocrystallization method of the present invention is selected from one of surface mechanical grinding treatment, surface mechanical rolling treatment, ultrasonic impact surface treatment, and rotational acceleration shot blasting treatment. Further, the surface nanocrystallization method is ultrasonic impact surface treatment.
More preferably, the structure of the heterogeneous tissue drill collar material is a heterogeneous layered structure, and the heterogeneous layered structure comprises recrystallized grains aggregated in a strip shape, refined ultra-fine grains, nano-crystals, nano-twin crystals and elongated deformed coarse crystals.
Ultra-fine grained material refers to grains having at least one dimension in three dimensions in the order of submicron (0.1< d <1 μm). The nano-crystal is a crystal grain with at least one dimension in three-dimensional space being in nanometer order (1< d <100nm), and the nano-twin crystal is a twin crystal with nanometer dimension and thickness. Coarse grain refers to a material with larger internal grains, and the strength and toughness of the material are relatively low.
Further preferably, the volume fraction of the ribbon-shaped aggregated recrystallization is generally 10-60%, the average grain size is 1-8 μm, the volume fraction of the nano twin crystal is 5-20%, the volume fraction of the nano crystal is 15-55%, and the volume fraction of the elongated deformed coarse crystal is 5-15%. According to the heterogeneous layered structure stainless steel prepared by the method, for example, the yield strength of the heterogeneous layered structure 316L stainless steel is 750-1250 MPa, the tensile strength is 850-1360 MPa, the uniform elongation is more than or equal to 10%, and the corrosion resistance is more than or equal to 25% higher than that of the heterogeneous layered structure 316L stainless steel.
The invention provides a heterogeneous tissue drill collar material, which is prepared by the preparation method of the high-strength and high-toughness heterogeneous tissue drill collar material.
Examples
The present invention will be specifically described below by way of examples. It should be noted that the following examples are only for illustrating the present invention and should not be construed as limiting the scope of the present invention, and that the insubstantial modifications and adaptations of the present invention by those skilled in the art based on the above disclosure are still within the scope of the present invention.
The equipment used in the examples was: a high-temperature box-type muffle furnace, ultrasonic surface nanocrystalline strengthening equipment and a medium-sized synchronous rolling mill.
Example 1
The embodiment provides a preparation method of a high-strength and high-toughness heterogeneous tissue drill collar material, which sequentially comprises the following steps:
solution treatment: putting the stainless steel plate into a 950 ℃ high-temperature box-type muffle furnace, preserving the heat for 360min, taking out the stainless steel plate, air-cooling the stainless steel plate to room temperature, and after solution treatment, obtaining coarse-grained stainless steel with uniform grain size, wherein the average grain size is about 65 mu m;
cold rolling treatment: carrying out cold rolling treatment on the stainless steel plate subjected to solution treatment at room temperature, wherein the reduction of each pass is 0.05mm, and finally, the plate is rolled to be 3.75mm, and the total rolling reduction is 75%;
and (3) incomplete recrystallization annealing treatment: finally, heating the high-temperature box type muffle furnace to 850 ℃, then putting the stainless steel plate subjected to surface nanocrystallization treatment into the muffle furnace, preserving the temperature for 25min, and quickly taking out the muffle furnace and cooling the stainless steel plate to room temperature;
surface nanocrystallization treatment: carrying out surface nanocrystallization treatment on the rolled stainless steel plate, and carrying out surface nanocrystallization treatment on a 316L stainless steel plate for 100min by using ultrasonic surface nanocrystal strengthening equipment to form a surface superfine nanocrystal layer with the thickness of 10 microns on the surface layer of the treated steel plate;
the stainless steel is a 316L stainless steel plate with the thickness of 5mm, and the stainless steel comprises the following components in percentage by mass: less than or equal to 0.03 wt% of C, less than or equal to 1.0 wt% of Si, less than or equal to 2.0 wt% of Mn, less than or equal to 0.045 wt% of P, less than or equal to 0.03 wt% of S, Ni: 10.0-14.0 wt%, Cr: 16.0 to 18.0 wt%, Mo: 2.0 to 3.0 wt%, and the balance Fe and inevitable impurities.
The embodiment also provides the drill collar material with the heterogeneous tissue, which is prepared by the preparation method of the drill collar material with the high strength and high toughness with the heterogeneous tissue.
The drill collar material with the heterogeneous layered structure, which is prepared by the method for preparing the drill collar material with the heterogeneous structure, has the surface superfine nanocrystalline layer, nanometer twin crystal, micron recrystallization and mixed residual elongation deformation coarse crystal phase, has the yield strength of 950MPa, the tensile strength of 1030MPa and the fracture elongation of-20 percent; for the untreated sample, the yield strength is 350MPa, and the tensile strength is 490MPaThe elongation at break is 40%. The samples reinforced in this example and the untreated samples were subjected to a slow strain rate tensile corrosion test (temperature: 200 ℃ C., strain rate: 4.5X 10)-6S, corrosive medium: 15% sodium chloride solution) were compared to find: the elongation at break of the sample strengthened by the embodiment is reduced from 20% to 18.2%; the elongation at break of the untreated sample decreased from 40% to 25%. Obviously, the stress corrosion resistance of the sample treated by the method is greatly improved. Therefore, the sample treated by the method can greatly promote the service performance of the drill rod in a severe environment, and can greatly prolong the service life of the drill rod working under severe working conditions.
Example 2
The embodiment provides a preparation method of a high-strength and high-toughness heterogeneous tissue drill collar material, which sequentially comprises the following steps:
solution treatment: putting the stainless steel plate into a high-temperature box-type muffle furnace at 1150 ℃ for heat preservation for 240min, taking out the stainless steel plate and air-cooling to room temperature, wherein the grain size of the coarse-grained stainless steel after solution treatment is relatively uniform, and the average grain size is about 55 mu m;
cold rolling treatment: carrying out cold rolling treatment on the stainless steel plate subjected to solution treatment at room temperature, wherein the reduction of each pass is 0.08mm, and finally, the plate is rolled to be 3mm, and the total rolling reduction is 60%;
and (3) incomplete recrystallization annealing treatment: heating a high-temperature box type muffle furnace to 800 ℃, then putting the stainless steel plate subjected to surface nanocrystallization treatment into the muffle furnace, preserving the temperature for 30min, and quickly taking out the muffle furnace and cooling the stainless steel plate to room temperature;
surface nanocrystallization treatment: carrying out surface nanocrystallization treatment on the rolled stainless steel plate, and carrying out surface nanocrystallization treatment on a 316L stainless steel plate for 150min by using ultrasonic surface nanocrystal strengthening equipment to form a surface superfine nanocrystal layer with the thickness of about 18.5 microns on the surface layer of the treated steel plate;
the stainless steel is a 316L stainless steel plate with the thickness of 5mm, and the stainless steel comprises the following components in percentage by mass: less than or equal to 0.03 wt% of C, less than or equal to 1.0 wt% of Si, less than or equal to 2.0 wt% of Mn, less than or equal to 0.045 wt% of P, less than or equal to 0.03 wt% of S, Ni: 10.0-14.0 wt%, Cr: 16.0 to 18.0 wt%, Mo: 2.0 to 3.0 wt%, and the balance Fe and inevitable impurities.
The embodiment also provides the drill collar material with the heterogeneous tissue, which is prepared by the preparation method of the drill collar material with the high strength and high toughness with the heterogeneous tissue.
The heterogeneous layered structure drill collar material with the surface ultrafine nanocrystalline layer, the nano twin crystal, the micron recrystallization and the mixed residual elongated deformation coarse crystal phase is prepared by the method for preparing the heterogeneous structure drill collar material, the yield strength can reach 870MPa, the tensile strength can reach 990MPa, and the fracture elongation is 25 percent; for the untreated sample, the yield strength is 350MPa, the tensile strength is 490MPa, and the elongation at break is 40%. The samples reinforced in this example and the untreated samples were subjected to a slow strain rate tensile corrosion test (temperature: 200 ℃ C., strain rate: 4.5X 10)-6S, corrosive medium: 15% sodium chloride solution) were compared to find: the elongation at break of the sample strengthened by the embodiment is reduced from 25% to 17.4%; the elongation at break of the untreated sample decreased from 40% to 25%. Obviously, the stress corrosion resistance of the sample treated by the method is greatly improved. Therefore, the sample treated by the method can greatly promote the service performance of the drill rod in a severe environment, and can greatly prolong the service life of the drill rod working under severe working conditions.
Comparative example 1
The specific implementation of the preparation method of the drill collar material is the same as that of example 1, but the preparation method sequentially comprises solution treatment, cold rolling treatment and incomplete recrystallization annealing treatment.
The embodiment also provides a drill collar material which is prepared according to the preparation method of the drill collar material.
The yield strength of the drill collar material obtained by the embodiment can reach 735MPa, the tensile strength can reach 790MPa, and the fracture elongation is 32 percent; the samples reinforced in this example were subjected to a slow strain rate tensile corrosion test (temperature: 200 ℃ C., strain rate: 4.5X 10)-6S, corrosive medium: 15% sodium chloride solution) was found: through this experimentThe elongation at break of the example strengthened sample decreased from 32% to 24%; compared with the example 1, the corrosion performance of the sample of the comparative example 1 which is subjected to the solution treatment, the cold rolling treatment and the incomplete recrystallization annealing treatment in sequence is lower than that of the sample which is subjected to the solution treatment, the cold rolling treatment, the incomplete recrystallization annealing treatment and the surface nanocrystallization treatment in sequence.
Comparative example 2
The specific implementation mode of the preparation method of the drill collar material is the same as that of example 1, but the difference is that in the surface nanocrystallization treatment, the rolled stainless steel plate is subjected to surface nanocrystallization treatment, ultrasonic surface nanocrystal strengthening equipment is used for performing surface nanocrystallization treatment on a 316L stainless steel plate for 300min, and a surface superfine nanocrystal layer with the thickness of 34 microns is formed on the surface layer of the treated steel plate.
The embodiment also provides a drill collar material which is prepared according to the preparation method of the drill collar material.
The yield strength of the drill collar material obtained by the embodiment can reach 1020MPa, the tensile strength can reach 1260MPa, and the breaking elongation is 18.1%; the samples reinforced in this example were subjected to a slow strain rate tensile corrosion test (temperature: 200 ℃ C., strain rate: 4.5X 10)-6S, corrosive medium: 15% sodium chloride solution) was found: the elongation at break of the sample strengthened by the embodiment is reduced from 18.6 percent to 17.4 percent; compared with the example 1, the further improvement of the thickness of the surface nanocrystalline layer can obviously improve the mechanical property and the corrosion property.
The foregoing examples are merely illustrative and serve to explain some of the features of the method of the present invention. The appended claims are intended to claim as broad a scope as is contemplated, and the examples presented herein are merely illustrative of selected implementations in accordance with all possible combinations of examples. Accordingly, it is applicants' intention that the appended claims are not to be limited by the choice of examples illustrating features of the invention. Also, where numerical ranges are used in the claims, subranges therein are included, and variations in these ranges are also to be construed as possible being covered by the appended claims.
Claims (10)
1. A preparation method of a high-strength high-toughness heterogeneous tissue drill collar material is characterized by comprising the following steps:
the heterogeneous structure drill collar material is obtained by sequentially carrying out solid solution treatment, cold rolling treatment, incomplete recrystallization annealing treatment and surface nanocrystallization treatment on stainless steel.
2. The method for preparing the high-strength and high-toughness heterogeneous structure drill collar material as claimed in claim 1, wherein in the solution treatment, the stainless steel is kept at 850-1150 ℃ for 20-600 min, and is air-cooled to room temperature to obtain an austenite structure, and the average grain size of the austenite structure is 30-130 μm.
3. The method for preparing the high-strength high-toughness heterogeneous structure drill collar material as claimed in claim 1, wherein in the cold rolling treatment, the total cold rolling reduction amount is 60-85%, and the cold rolling speed is less than or equal to 12 m/min.
4. The method for preparing a high-strength high-toughness heterogeneous-structure drill collar material according to claim 1, wherein in the incomplete recrystallization annealing treatment, the annealing temperature is 700-900 ℃ and the annealing time is 5-60 min.
5. The method for preparing the high-strength high-toughness heterogeneous tissue drill collar material as claimed in claim 1, wherein a surface ultrafine nanocrystalline layer with a thickness of 10-45 μm is formed after the surface nanocrystallization treatment.
6. The method for preparing the high-strength high-toughness heterogeneous tissue drill collar material as claimed in claim 4, wherein in the surface nanocrystallization, the surface nanocrystallization time is 30-360 min, and the surface nanocrystallization frequency is not less than 36690 times/m2。
7. The method for preparing a high strength and high toughness isomerous tissue drill collar material as claimed in claim 1, wherein said surface nanocrystallization is selected from one of surface mechanical grinding, surface mechanical rolling, ultrasonic impact surface treatment and rotational accelerated shot blasting.
8. The method for preparing the high-strength high-toughness heterogeneous tissue drill collar material according to any one of claims 1 to 7, wherein the structure of the heterogeneous tissue drill collar material is a heterogeneous layered structure, and the heterogeneous layered structure comprises recrystallized grains aggregated in a strip shape, refined ultrafine grains, nano-crystals, nano-twin crystals and elongation deformation coarse grains.
9. The method for preparing a high-strength high-toughness isomerous tissue drill collar material as claimed in claim 8, wherein the volume fraction of recrystallized grains in the strip-like aggregation is generally 10-60%, the average grain size is 1-8 μm, the volume fraction of nano twin crystals is 5-20%, the volume fraction of nano crystals is 15-55%, and the volume fraction of elongated deformed coarse crystals is 5-15%.
10. The drill collar material with the heterogeneous structure is characterized by being prepared by the preparation method of the drill collar material with the high strength and the high toughness according to any one of claims 1 to 9.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202011211849.5A CN112430710A (en) | 2020-11-03 | 2020-11-03 | Preparation method of high-strength and high-toughness heterogeneous tissue drill collar material and drill collar material |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202011211849.5A CN112430710A (en) | 2020-11-03 | 2020-11-03 | Preparation method of high-strength and high-toughness heterogeneous tissue drill collar material and drill collar material |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| CN112430710A true CN112430710A (en) | 2021-03-02 |
Family
ID=74695168
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN202011211849.5A Pending CN112430710A (en) | 2020-11-03 | 2020-11-03 | Preparation method of high-strength and high-toughness heterogeneous tissue drill collar material and drill collar material |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN112430710A (en) |
Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN113720663A (en) * | 2021-08-04 | 2021-11-30 | 西南交通大学 | Method for preparing high-strength-toughness isomeric nickel by regulating and controlling rolling annealing process |
| CN113941602A (en) * | 2021-09-29 | 2022-01-18 | 西安交通大学 | Gradient-structure metal material with adjustable gradient rate and preparation method thereof |
| CN113953315A (en) * | 2021-09-29 | 2022-01-21 | 西安交通大学 | Layered multilevel heterostructure metal material with adjustable period and preparation method thereof |
| CN114622074A (en) * | 2022-05-12 | 2022-06-14 | 中北大学 | Austenitic stainless steel, heat treatment process thereof and application of heat treatment process |
| CN116213751A (en) * | 2022-12-13 | 2023-06-06 | 浙江大学 | 316L stainless steel surface treatment method |
| CN116516121A (en) * | 2023-05-16 | 2023-08-01 | 广东海洋大学 | 321 austenitic stainless steel belt with lamellar crystal grain size isomerism and preparation method thereof |
Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN106086344A (en) * | 2016-07-28 | 2016-11-09 | 中国科学院金属研究所 | A kind of metal material roller type method for making Nano surface |
| CN108359780A (en) * | 2018-04-09 | 2018-08-03 | 西南交通大学 | The method for improving metastable state austenite stainless hardness of steel and anti-stress corrosion performance |
| CN109811271A (en) * | 2017-11-20 | 2019-05-28 | 南京理工大学 | A kind of preparation method of heterogeneous layer structure 316L stainless steel |
-
2020
- 2020-11-03 CN CN202011211849.5A patent/CN112430710A/en active Pending
Patent Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN106086344A (en) * | 2016-07-28 | 2016-11-09 | 中国科学院金属研究所 | A kind of metal material roller type method for making Nano surface |
| CN109811271A (en) * | 2017-11-20 | 2019-05-28 | 南京理工大学 | A kind of preparation method of heterogeneous layer structure 316L stainless steel |
| CN108359780A (en) * | 2018-04-09 | 2018-08-03 | 西南交通大学 | The method for improving metastable state austenite stainless hardness of steel and anti-stress corrosion performance |
Cited By (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN113720663A (en) * | 2021-08-04 | 2021-11-30 | 西南交通大学 | Method for preparing high-strength-toughness isomeric nickel by regulating and controlling rolling annealing process |
| CN113720663B (en) * | 2021-08-04 | 2022-06-10 | 西南交通大学 | Method for preparing high-strength-toughness isomeric nickel by regulating and controlling rolling annealing process |
| CN113941602A (en) * | 2021-09-29 | 2022-01-18 | 西安交通大学 | Gradient-structure metal material with adjustable gradient rate and preparation method thereof |
| CN113953315A (en) * | 2021-09-29 | 2022-01-21 | 西安交通大学 | Layered multilevel heterostructure metal material with adjustable period and preparation method thereof |
| CN114622074A (en) * | 2022-05-12 | 2022-06-14 | 中北大学 | Austenitic stainless steel, heat treatment process thereof and application of heat treatment process |
| CN116213751A (en) * | 2022-12-13 | 2023-06-06 | 浙江大学 | 316L stainless steel surface treatment method |
| CN116516121A (en) * | 2023-05-16 | 2023-08-01 | 广东海洋大学 | 321 austenitic stainless steel belt with lamellar crystal grain size isomerism and preparation method thereof |
| CN116516121B (en) * | 2023-05-16 | 2023-12-01 | 广东海洋大学 | 321 austenitic stainless steel belt with lamellar crystal grain size isomerism and preparation method thereof |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN112430710A (en) | Preparation method of high-strength and high-toughness heterogeneous tissue drill collar material and drill collar material | |
| EP2865775B1 (en) | Steel for oil well pipe, oil well pipe, and method for producing same | |
| JP5344454B2 (en) | Steel for warm working, warm working method using the steel, and steel and steel parts obtained thereby | |
| AU2015291875B2 (en) | Low alloy oil-well steel pipe | |
| CA2888154C (en) | Low alloy steel for oil country tubular goods having excellent sulfide stress cracking resistance and manufacturing method therefor | |
| CN108300915B (en) | Al-Zn-Mg-Cu aviation aluminum alloy and preparation method thereof | |
| TW202039881A (en) | Steel sheet, manufacturing method thereof, and formed product | |
| Deng et al. | Extending the boundaries of mechanical properties of Ti-Nb low-carbon steel via combination of ultrafast cooling and deformation during austenite-to-ferrite transformation | |
| CN114921731A (en) | Ultra-high-strength high-performance medium plate maraging stainless steel and preparation method thereof | |
| Mi et al. | Effects of annealing temperature on the microstructure and properties of the 25Mn-3Si-3Al TWIP steel | |
| Dobrzański et al. | Thermo-mechanical processing and microstructure evolution of high-manganese austenitic TRIP-type steels | |
| Chen et al. | A new approach of a gradient nanograined surface layer for Mg-3Al-1Zn alloy induced by SMRGT | |
| JP2007302937A (en) | Steel plate for hardened member, hardened member and manufacturing methods thereof | |
| Wang et al. | Microstructures and Mechanical Properties of an Ultrahigh‐Strength and Ductile Medium‐Carbon High‐Silicon Spring Steel | |
| JP2019019396A (en) | Nitrided component and nitriding treatment method | |
| Zhu et al. | Effect of rare earth Y on microstructure and texture of oriented silicon steel during hot rolling and cold rolling processes | |
| CN116702526A (en) | Modeling and manufacturing method of high-speed turnover plow grid bar capable of improving mechanical property and reducing resistance | |
| Vdovin et al. | Investigation of microstructure of high-manganese steel, modified by ultra-dispersed powders, on the base of compounds of refractory metals | |
| Dobrzański | Effects of chemical composition and processing conditions on the structure and properties of high-speed steels | |
| Li et al. | Effect of Cooling Condition on Fatigue Behavior of the Forged EA4T Steel | |
| JPS6132384B2 (en) | ||
| Cai et al. | An experimental investigation on B2 phase transfer and grain boundary character on mechanical properties of rapidly cooled Fe–6.5 wt% Si alloy | |
| CN111440995A (en) | Method for manufacturing small-aperture ring die | |
| Mazahery et al. | An Investigation on Mechanical Properties of Ultrafine Grained 316 Stainless Steel by Thermomechanical Treatment | |
| Seikh et al. | Evaluation of Strength and Microstructural Properties of Heat Treated High-Molybdenum Content Maraging Steel. Crystals 2021, 11, 1446 |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| PB01 | Publication | ||
| PB01 | Publication | ||
| SE01 | Entry into force of request for substantive examination | ||
| SE01 | Entry into force of request for substantive examination |