[go: up one dir, main page]
More Web Proxy on the site http://driver.im/

CN110129658A - A kind of high manganese nitrogen-free type high-strength and high ductility anti-hydrogen embrittlement austenitic stainless steel and preparation method - Google Patents

A kind of high manganese nitrogen-free type high-strength and high ductility anti-hydrogen embrittlement austenitic stainless steel and preparation method Download PDF

Info

Publication number
CN110129658A
CN110129658A CN201910447345.4A CN201910447345A CN110129658A CN 110129658 A CN110129658 A CN 110129658A CN 201910447345 A CN201910447345 A CN 201910447345A CN 110129658 A CN110129658 A CN 110129658A
Authority
CN
China
Prior art keywords
stainless steel
strength
hydrogen embrittlement
austenitic stainless
preparation
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.)
Granted
Application number
CN201910447345.4A
Other languages
Chinese (zh)
Other versions
CN110129658B (en
Inventor
宿彦京
何隽
郭梓辉
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
University of Science and Technology Beijing USTB
Original Assignee
University of Science and Technology Beijing USTB
Priority date (The priority date 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 date listed.)
Filing date
Publication date
Application filed by University of Science and Technology Beijing USTB filed Critical University of Science and Technology Beijing USTB
Priority to CN201910447345.4A priority Critical patent/CN110129658B/en
Publication of CN110129658A publication Critical patent/CN110129658A/en
Application granted granted Critical
Publication of CN110129658B publication Critical patent/CN110129658B/en
Active legal-status Critical Current
Anticipated expiration legal-status Critical

Links

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
    • C21D1/18—Hardening; Quenching with or without subsequent 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
    • 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
    • C21D8/005—Modifying the physical properties by deformation combined with, or followed by, heat treatment of ferrous alloys
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C33/00—Making ferrous alloys
    • C22C33/04—Making ferrous alloys by melting
    • 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
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/20—Ferrous alloys, e.g. steel alloys containing chromium with copper
    • 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
    • C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
    • 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
    • C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
    • 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
    • C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—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

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Steel (AREA)

Abstract

A kind of high manganese nitrogen-free type high-strength and high ductility anti-hydrogen embrittlement austenitic stainless steel and manufacturing method, its chemical component are as follows: C < 0.05%, Si < 0.50%, Mn:6~10%, Cr:12~16%, Ni:4.5~6.5%, Mo:0.5~3%, S < 0.01%, P < 0.03%, surplus are Nb, Ti, V, Al, Cu and inevitable impurity element of Fe and micro addition.Manufacturing method includes smelting the processing steps such as (casting), forging (hot rolling), rolling, tempering.High-strength, high-toughness stainless steel feature produced by the present invention is based on 13Cr-5Ni-2Mo/15Cr-6Ni-2Mo super martensitic stainless steel, austenitizing is carried out by adding cheap Mn element, strengthened by remaining martensite back stress and the refined crystalline strengthening of austenitic matrix realizes high intensity, high tenacity is obtained by phase transformation, the anti-H of material is improved by austenitizing2S (hydrogen embrittlement) stress corrosion performance.High-strength steel produced by the present invention in kept corrosion proof while possessing high toughness and hydrogen embrittlement energy.Present invention process is simple, Yi Shixian industrialization, can be used in containing H2It the oil pipe of S oil (gas) and is used in corrosion resistance and the demanding environment of anti-hydrogen embrittlement.

Description

A kind of high manganese nitrogen-free type high-strength and high ductility anti-hydrogen embrittlement austenitic stainless steel and preparation method
Technical field
The present invention relates to high-strength and high ductility anti-hydrogen embrittlement austenitic stainless steels of a kind of high-manganese low-carbon nitrogen-free and preparation method thereof, especially It is related to it is a kind of can be used as deep-well oil-gas pipeline material and crude oil, natural gas conveying equipment material high strength stainless steel.
Background technique
The general 13Cr/15Cr type stainless steel in China is mainly martensitic stain less steel, and main alloy element is C and Cr. Such steel because of its hardness with higher, cheap cost and widely used.Regrettably due to a large amount of C's Addition will form Cr23C6, reduce effective Cr content, while the Cr generated23C6Easy segregation leads to intercrystalline corrosion in crystal boundary.Therefore, In more harsh Service Environment, corrosion resisting property faces severe challenge conventional martensitic stainless steel；Meanwhile research finds to pass System 13Cr type martensitic stain less steel can generate H2S stress corrosion.In order to overcome the above problem of conventional martensitic stainless steel, develop By improve Cr constituent content and add Mo member usually improve material corrosion resisting property and anti-H2S stress corrosion performance, thus A certain amount of Ni element need to may be further added, make material complete austenitizing, it is ensured that full martensitic structure.
The nineties, foreign countries develop carbon containing minute quantity, the super 13Cr/15Cr stainless steel of the modified of appropriate nickel and molybdenum.But In this steel, the maximum hardness in terms of HRC is also constrained to 27 (referring to NACE MR0175-2001).Above-mentioned modified is super 13Cr/15Cr stainless steel, it is proposed that several steel with high mechanical strength and excellent anticorrosive performance.For example, international monopoly WO2017/162160 A1 discloses a kind of resistance to H2The martensitic stain less steel tubing and casing of S stress corrosion cracking, chemical element matter Measure percentage main feature are as follows: C: < 0.05%, Cr:11~14%, Ni:4~7%, Mo:1.5~2.5%；Metal structure is main It, can be in the CO of high concentration by tempered martensite2、Cl-Etc. oil well, the gas of crude oil or natural gas under the strong corrosive environment coexisted In well, but its H2S suitable environment is limited at 0.01MPa, while intensity is also only in 95ksi.International monopoly WO2005/ 007915A1 disclose it is a kind of than super 13Cr steel have more superior anti-H2S stress corrosion martensitic stain less steel, it is main special Sign promotes corrosion resistance and anti-H 3.5~7% to be no more than 10% by addition Mo maximum, by control solid solution Mo content2S (hydrogen It is crisp) stress corrosion ability.Such martensitic stain less steel has high-strength mechanical strength, and in CO2There is excellent corrosion resistant in environment Corrosion, but applicable H2S partial pressure is only 0.003MPa.
Domestic related patents have also done modification to traditional 13Cr martensitic stain less steel.For example, CN1571858 provides one kind The martensitic stain less steel of Mo and Cu is added, which has excellent halophile stress corrosion, corrosion-resistant mill Damage property and resistance to local corrosion；CN102534419 provides another method of modifying: reducing C content to 0~0.03%, improves For Ni content to 4~6%, Mo content 1~2%, which has high-strength and high ductility, good resistance to local corrosion performance.
For 13Cr/15Cr type super martensitic stainless steel modified above, it is limited by its martensitic matrix, is typically resulted in Its toughness is lower, at the same in high intensity levels (more than X110, X125 rank etc.) to H2S stress corrosion is very sensitive.
Summary of the invention
With the development of AOD/VOD refining techniques, the control of P, S impurity content is further accurate in steel, and alloying component is into one Step optimization is possibly realized.Strict control S element, which can be realized Mn constituent content and reach very high and not generate MnS bulky grain, to be mingled with. In view of the problems of the existing technology, the present invention is based on existing 13Cr-5Ni-2Mo/15Cr-6Ni-2Mo type super martensitics not Become rusty steel, is related to a kind of pass through and adds cheap element M n reduction Ms point, realizes austenitizing, and providing one kind can industrialized production Preparation flow method, easily realize industrialization, industrialization, generate huge economic interests.
A kind of high manganese nitrogen-free type high-strength and high ductility anti-hydrogen embrittlement austenitic stainless steel, the mass percentage content of chemical component Are as follows: C < 0.05%, Si < 0.50%, Mn:6~10%, Cr:12~16%, Ni:4.5~6.5%, Mo:0.5~3%, S < 0.01%, P < 0.02%, surplus are Nb, Ti, V, Al, Cu element and inevitable impurity element of Fe and micro addition.
Further, when Cr content is greater than 15%, Ni content needs to be greater than 5.5%, to ensure material in high temperature solid solution State is formed without ferrite.
A kind of preparation method of high manganese nitrogen-free type high-strength and high ductility anti-hydrogen embrittlement austenitic stainless steel as described above, preparation step It is as follows:
(1) it uses and smelts, casts, obtaining meeting above-mentioned chemical component requirement high-strength and high ductility austenitic stainless steel slab；
(2) in 1100 DEG C~1300 DEG C forgings or hot rolling molding；
(3) molding high-strength, high-toughness stainless steel is subjected to cold-rolling treatment, overall reduction is 35%~55%；
(4) stainless steel after cold rolling is subjected to tempering, 600 DEG C~800 DEG C of tempering temperature, obtains varying strength rank High-strength and high ductility austenitic stainless steel, including 110ksi, 125ksi etc..
Further, the preparation of the austenitic stainless steel is based on the super horse of 13Cr-5Ni-2Mo/15Cr-6Ni-2Mo Family name's body stainless steel, addition inexpensive alloy element M n reduce martensite transformation temperature (Ms), carry out austenitizing；Pass through phase transition process Fining austenite grains carry out back stress reinforcing to austenitic matrix by remaining martensite；Refined crystalline strengthening and back stress are strengthened The movement for inhibiting deformation initial stage dislocation, makes material obtain high yield strength.
Further, enter the moulding stage in material, dislocation starts proliferation and starts, and the stability of austenitic matrix is by broken Bad, martensite transfor mation takes place, and phase transformation makes the high-strength steel of manufacture obtain high tenacity.
In the technical scheme, other inevitable trace impurities are mainly S, P, O and N.
The influence of S
S is the anti-H for influencing steel2The important element of S (hydrogen embrittlement) stress corrosion ability, leads to steel anisotropy, in transverse direction Deteriorate with toughness on thickness direction, influences the low-temperature impact toughness of material.Meanwhile S can form MnS with Mn and be mingled with greatly, deteriorate material The mechanical property of material influences the threshold value that Mn element is added in steel grade.
The influence of P
P can significantly reduce the low-temperature impact toughness of steel, improve the ductile-brittle transition temperature of steel, steel occur cold short.P member simultaneously Cellulose content can be in cyrystal boundary segregation, the mechanical performance of severe exacerbation material when being more than threshold value.
The influence of O
O element mainly exists in the form of the oxide in steel, to the hot-working character, impact flexibility and corrosion resistance of steel There can be detrimental effect.
The influence of N
N is the beneficial element added in steel, can improve the pitting resistance of stainless steel, while N also can be used as austenite Energy element balance Cr equivalent, generates stainless steel without ferrite in high temperature solid solution state.But high-strength and high ductility Ovshinsky of the invention Body stainless steel is related to the tempering process at 600~800 DEG C, this temperature range is the strong Precipitation temperature range of CrN, and CrN can be anxious Speed deteriorates the mechanical property of material, it is therefore desirable to strict control N element content.
Typical organization of the high-strength and high ductility austenitic stainless steel of the present invention after manufacturing process described above at room temperature is residual The fine grain austenite of remaining martensite and recrystallization, wherein fine grain austenite is broadly divided into the isometric austenite grown with diffusion With the lath-shaped austenite grown in the form of shear.
The present invention has compared with the 13Cr-5Ni-2Mo/15Cr-6Ni-2Mo super martensitic stainless steel of the prior art It is following the utility model has the advantages that
1. high-strength and high ductility austenitic stainless steel of the present invention is by adding cheap Mn element austenitizing, compared to Ni Element cost only have its 1/10th, the mechanical performance of material, strict control are greatly improved while increasing few cost Production cost.
2. high-strength and high ductility austenitic stainless steel of the present invention can reach very high strength rank (110ksi, 125ksi Deng), in had corrosion proof while there is excellent anti-H2S (hydrogen embrittlement) stress corrosion ability.
3. high-strength and high ductility austenitic stainless steel simple production process of the present invention, it is easy to accomplish industrialization, industrialization, Generate great economic benefit.
Detailed description of the invention
Fig. 1 is embodiment EBSD contrast figure；
Fig. 2 is embodiment engineering stress strain curve；
Fig. 3 is dynamic potential polarization curve of the embodiment and comparative example in four kinds of solution,
a)0.2M NaSO4；b)0.1M HNO3；c)0.2M NaOH；D) 3.5%NaCl；
Fig. 4 is embodiment and comparative example CO2Corrosion test rear surface pattern,
A) and b) USTB13Cr；C) and d) S13Cr.；
Fig. 5 be embodiment and comparative example step stress test as a result,
a)USTB13Cr；b)S13Cr..
Specific embodiment
Embodiment and comparative example
Table 1 is that the high-strength and high ductility austenitic stainless steel (being denoted as USTB13Cr) being related to and factory's commodity production manufacture The chemical component of 13Cr-5Ni-2Mo super martensitic stainless steel (being denoted as S13Cr) matches.
1 embodiment of table and comparative example chemical component
Surplus is Fe and inevitable impurity element in table 1.
The heat treatment process of embodiment is hot forging (playing 1200 DEG C of temperature of forging), cold rolling (overall reduction 44%), tempering (700 DEG C keep the temperature 1 hour).
Embodiment electron backscatter diffraction figure (EBSD) is as shown in Figure 1.The main microstructure of embodiment is for fine grained region and slightly Crystalline region.Wherein fine grained region is the austenite of Nano grade and the admixture that remaining martensite mentions.Coarse grain zone is non-recrystallization Retained austenite, retained austenite are formed streaky structure by rolling process, are distributed martensite between strip austenite.
Embodiment engineering stress strain curve is as shown in Figure 2.Embodiment USTB13Cr yield strength 932MPa (reaches 125ksi intensity rank), tensile strength 1085MPa, elongation percentage 33.2%, uniform elongation 29%.The super horse of comparative example S13Cr Family name's body stainless steel yield strength 912MPa, tensile strength 1030MPa, elongation percentage 16.3%.Under conditions of same intensity circle, Embodiment toughness greatly improves.
Embodiment and comparative example dynamic potential polarization curve in acid-alkali salt is as shown in Figure 3.In alkalinity and neutral solution, The corrosion potential of USTB13Cr ratio S13Cr is more preferable, shows smaller corrosion tendency.In strongly acidic solution, USTB13Cr Similar with S13Cr corrosion potential, the corrosion current density of USTB13Cr is higher, and corrosion resistance is declined slightly.
Embodiment and comparative example CO2Corrosion test result as shown in figure 4, experiment condition be in the solution of 3.5%NaCl, CO21MPa is divided, 120 DEG C of temperature, experimental period is 720 hours.
Faint yellow Product Films are locally adhered on comparative example surface.A thin layer of Product Films are adhered on embodiment surface, still keep Preferable anti-CO2Corrosive power.Embodiment and comparative example measures threshold stress with step stress test in simulation hydrogen environment Experimental result is as shown in Figure 5.Simulated solution is 0.2mol/L NaOH+0.22g/L thiocarbamide.Being flushed with hydrogen current density is 2mA/cm2。
Comparative example S13Cr threshold intensity is 613MPa, and embodiment USTB13Cr threshold intensity is 860MPa, and threshold intensity increases Add 40%, the anti-H of material is greatly improved2The ability of S stress corrosion (hydrogen embrittlement).

Claims (5)

1. a kind of high manganese nitrogen-free type high-strength and high ductility anti-hydrogen embrittlement austenitic stainless steel, which is characterized in that the quality percentage of chemical component Compare content are as follows: C < 0.05%, Si < 0.50%, Mn:6~10%, Cr:12~16%, Ni:4.5~6.5%, Mo:0.5~3%, S < 0.01%, P < 0.02%, surplus are Nb, Ti, V, Al, Cu element and inevitable impurity element of Fe and micro addition.
2. high-strength and high ductility austenitic stainless steel according to claim 1, it is characterised in that when Cr content is greater than 15%, Ni Content needs to be greater than 5.5%, to ensure that material is formed in high temperature solid solution state without ferrite.
3. a kind of preparation method of high manganese nitrogen-free type high-strength and high ductility anti-hydrogen embrittlement austenitic stainless steel as described in claim 1, It is characterized in that following the steps below:
(1) it uses and smelts, casts, obtaining meeting above-mentioned chemical component requirement high-strength and high ductility austenitic stainless steel slab；
(2) in 1100 DEG C~1300 DEG C forgings or hot rolling molding；
(3) molding high-strength, high-toughness stainless steel is subjected to cold-rolling treatment, overall reduction is 35%~55%；
(4) stainless steel after cold rolling is subjected to tempering, 600 DEG C~800 DEG C of tempering temperature, it is other high obtains different intensity scale Strong high-ductility austenitic stainless steel, including 110ksi, 125ksi.
4. the preparation method of high manganese nitrogen-free type high-strength and high ductility anti-hydrogen embrittlement austenitic stainless steel as claimed in claim 3, feature The preparation for being austenitic stainless steel is added honest and clean based on 13Cr-5Ni-2Mo/15Cr-6Ni-2Mo super martensitic stainless steel Valence alloying element Mn reduces martensite transformation temperature (Ms), carries out austenitizing；By phase transition process fining austenite grains, lead to It crosses remaining martensite and back stress reinforcing is carried out to austenitic matrix；Refined crystalline strengthening and back stress, which are strengthened, inhibits deformation initial stage dislocation Movement, makes material obtain high yield strength.
5. the preparation method of high manganese nitrogen-free type high-strength and high ductility anti-hydrogen embrittlement austenitic stainless steel as claimed in claim 4, feature It is to enter the moulding stage in material, dislocation starts proliferation and starts, and the stability of austenitic matrix is destroyed, martensite transfor mation Take place, phase transformation makes the high-strength steel of manufacture obtain high tenacity.
CN201910447345.4A 2019-05-27 2019-05-27 High-manganese nitrogen-free high-strength high-toughness hydrogen embrittlement-resistant austenitic stainless steel and preparation method thereof Active CN110129658B (en)

Priority Applications (1)

Application Number Priority Date Filing Date Title
CN201910447345.4A CN110129658B (en) 2019-05-27 2019-05-27 High-manganese nitrogen-free high-strength high-toughness hydrogen embrittlement-resistant austenitic stainless steel and preparation method thereof

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
CN201910447345.4A CN110129658B (en) 2019-05-27 2019-05-27 High-manganese nitrogen-free high-strength high-toughness hydrogen embrittlement-resistant austenitic stainless steel and preparation method thereof

Publications (2)

Publication Number Publication Date
CN110129658A true CN110129658A (en) 2019-08-16
CN110129658B CN110129658B (en) 2020-07-10

Family

ID=67582069

Family Applications (1)

Application Number Title Priority Date Filing Date
CN201910447345.4A Active CN110129658B (en) 2019-05-27 2019-05-27 High-manganese nitrogen-free high-strength high-toughness hydrogen embrittlement-resistant austenitic stainless steel and preparation method thereof

Country Status (1)

Country Link
CN (1) CN110129658B (en)

Cited By (10)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN111041349A (en) * 2019-11-26 2020-04-21 中国石油天然气集团有限公司 High-chromium alloy corrosion-resistant continuous pipe and preparation method thereof
CN111659732A (en) * 2020-06-08 2020-09-15 首钢集团有限公司 Method for solving corrosion of high-manganese hot-formed steel after pickling
CN111733367A (en) * 2020-07-08 2020-10-02 东莞理工学院 High-strength steel with nanometer, layered and metastable bone tissue and preparation method thereof
CN113136533A (en) * 2021-04-15 2021-07-20 鞍钢股份有限公司 Austenitic stainless steel for low temperature and manufacturing method thereof
CN113755753A (en) * 2021-08-24 2021-12-07 北京科技大学 Heterogeneous structure based multi-type strengthened austenitic stainless steel and manufacturing method thereof
CN114107630A (en) * 2021-11-19 2022-03-01 北京科技大学 Heat treatment method for improving hydrogen embrittlement resistance of martensitic stainless steel, stainless steel and application
CN116083819A (en) * 2023-03-20 2023-05-09 杭州铭赫科技有限公司 High-strength austenitic stainless steel powder and preparation method thereof
CN116117278A (en) * 2021-11-17 2023-05-16 华南理工大学 Austenitic stainless steel hydrogen embrittlement-resistant weldment for hydrogen energy equipment and preparation method
CN116219277A (en) * 2022-12-16 2023-06-06 桂林理工大学 High-strength stainless steel material and preparation method thereof
CN117444552A (en) * 2023-12-25 2024-01-26 中北大学 Method for improving hydrogen embrittlement resistance of 316L stainless steel hydrogen conveying pipe

Citations (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2003129192A (en) * 2001-10-24 2003-05-08 Nisshin Steel Co Ltd AUSTENITIC STAINLESS STEEL SUPERIOR IN STEAM OXIDATION RESISTANCE, CARBURIZATION RESISTANCE, AND sigma EMBRITTLEMENT RESISTANCE
CN1833043A (en) * 2003-06-10 2006-09-13 住友金属工业株式会社 Austenitic stainless steel for hydrogen gas and method for production thereof
CN105200340A (en) * 2015-09-23 2015-12-30 宝钢不锈钢有限公司 800-1,600 MPa grade high strength austenitic stainless steel, manufacturing method and warm forming method

Patent Citations (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2003129192A (en) * 2001-10-24 2003-05-08 Nisshin Steel Co Ltd AUSTENITIC STAINLESS STEEL SUPERIOR IN STEAM OXIDATION RESISTANCE, CARBURIZATION RESISTANCE, AND sigma EMBRITTLEMENT RESISTANCE
CN1833043A (en) * 2003-06-10 2006-09-13 住友金属工业株式会社 Austenitic stainless steel for hydrogen gas and method for production thereof
CN105200340A (en) * 2015-09-23 2015-12-30 宝钢不锈钢有限公司 800-1,600 MPa grade high strength austenitic stainless steel, manufacturing method and warm forming method

Cited By (15)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN111041349A (en) * 2019-11-26 2020-04-21 中国石油天然气集团有限公司 High-chromium alloy corrosion-resistant continuous pipe and preparation method thereof
CN111659732A (en) * 2020-06-08 2020-09-15 首钢集团有限公司 Method for solving corrosion of high-manganese hot-formed steel after pickling
CN111733367A (en) * 2020-07-08 2020-10-02 东莞理工学院 High-strength steel with nanometer, layered and metastable bone tissue and preparation method thereof
CN111733367B (en) * 2020-07-08 2021-07-09 东莞理工学院 High-strength steel with nanometer, layered and metastable bone tissue and preparation method thereof
CN113136533A (en) * 2021-04-15 2021-07-20 鞍钢股份有限公司 Austenitic stainless steel for low temperature and manufacturing method thereof
CN113755753A (en) * 2021-08-24 2021-12-07 北京科技大学 Heterogeneous structure based multi-type strengthened austenitic stainless steel and manufacturing method thereof
CN116117278A (en) * 2021-11-17 2023-05-16 华南理工大学 Austenitic stainless steel hydrogen embrittlement-resistant weldment for hydrogen energy equipment and preparation method
CN116117278B (en) * 2021-11-17 2023-09-26 华南理工大学 Austenitic stainless steel hydrogen embrittlement-resistant weldment for hydrogen energy equipment and preparation method
CN114107630B (en) * 2021-11-19 2022-08-19 北京科技大学 Heat treatment method for improving hydrogen brittleness resistance of martensitic stainless steel, stainless steel and application
CN114107630A (en) * 2021-11-19 2022-03-01 北京科技大学 Heat treatment method for improving hydrogen embrittlement resistance of martensitic stainless steel, stainless steel and application
CN116219277A (en) * 2022-12-16 2023-06-06 桂林理工大学 High-strength stainless steel material and preparation method thereof
CN116219277B (en) * 2022-12-16 2024-05-28 桂林理工大学 High-strength stainless steel material and preparation method thereof
CN116083819A (en) * 2023-03-20 2023-05-09 杭州铭赫科技有限公司 High-strength austenitic stainless steel powder and preparation method thereof
CN117444552A (en) * 2023-12-25 2024-01-26 中北大学 Method for improving hydrogen embrittlement resistance of 316L stainless steel hydrogen conveying pipe
CN117444552B (en) * 2023-12-25 2024-03-12 中北大学 Method for improving hydrogen embrittlement resistance of 316L stainless steel hydrogen conveying pipe

Also Published As

Publication number Publication date
CN110129658B (en) 2020-07-10

Similar Documents

Publication Publication Date Title
CN110129658A (en) A kind of high manganese nitrogen-free type high-strength and high ductility anti-hydrogen embrittlement austenitic stainless steel and preparation method
CN100507061C (en) High collapse-resistance and hydrogen sulphide-corrosion-resistant low alloy petroleum case pipe and method of manufacturing the same
CN101994066B (en) Deformation induced maraging stainless steel and machining process thereof
CN103320705B (en) Preparation method for CO2 corrosion resistant pipeline steel used for surface gathering
CN109536850B (en) High-strength-toughness low-yield-ratio thick steel plate and production process thereof
CN102534418A (en) Martensitic stainless steel for oil casing and manufacturing method thereof
CN101956146A (en) High strength super-martensitic stainless steel for oil and gas pipelines and preparation method thereof
EP4261320A1 (en) High-strength and toughness free-cutting non-quenched and tempered round steel and manufacturing method therefor
CN105506472A (en) 560MPa grade hot rolled steel plate for deep sea pipeline and production method thereof
US20230167522A1 (en) High Strength, High-Temperature Corrosion Resistant Martensitic Stainless Steel and Manufacturing Method Therefor
CN113136533B (en) Austenitic stainless steel for low temperature and manufacturing method thereof
CN105154765A (en) Seamless steel tube with high strength and toughness and manufacturing method thereof
CN102453841A (en) Steel used for sea oil extraction platform R4S grade mooring chain and its manufacture method
CN106756489A (en) 450 grades of anti-crack high-strength abrasion-proof steels of Brinell hardness and its manufacture method
CN101307413A (en) Microalloying steel for ultra-high-strength sucker rod
CN103469097B (en) The corrosion-resistant tubing and casing of high strength martensitic ferrite diphasic stainless steel and manufacture method thereof
CN112458367B (en) High-strength intergranular corrosion-resistant twinning-induced plasticity austenitic stainless steel
CN111218624B (en) Carbon dioxide corrosion resistant seamless steel pipe and preparation method thereof
CN104264058A (en) Biphasic stainless steel line pipe with yield strength of 555 MPa or above and manufacturing method thereof
CN116200682B (en) High-strength high-toughness low Wen Haigong steel plate and manufacturing method thereof
CN100545290C (en) A kind of thermal treatment ultra-fine crystal D grade sucker rod sucker rod of exempting from is with steel and production method
CN115369323B (en) 800 MPa-level hydrogen-induced crack resistant container steel plate and production method thereof
CN116377343B (en) Marine engineering steel plate serving in polar region marine environment and manufacturing method thereof
Yu et al. Effect of deep tempering on microstructure and mechanical properties of G13Cr4Mo4Ni4V steel
CN105734437B (en) A kind of bar-shaped copper precipitated phase Strengthening and Toughening marine steel plate of nanoscale and preparation method thereof

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
GR01 Patent grant
GR01 Patent grant