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WO2025171013A1 - Procédé de modification de surface d'aciers inoxydables utilisés dans des environnements de sel fondu - Google Patents

Procédé de modification de surface d'aciers inoxydables utilisés dans des environnements de sel fondu

Info

Publication number
WO2025171013A1
WO2025171013A1 PCT/US2025/014603 US2025014603W WO2025171013A1 WO 2025171013 A1 WO2025171013 A1 WO 2025171013A1 US 2025014603 W US2025014603 W US 2025014603W WO 2025171013 A1 WO2025171013 A1 WO 2025171013A1
Authority
WO
WIPO (PCT)
Prior art keywords
bulk material
stainless steel
molten salt
chamber
nitrided
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
Application number
PCT/US2025/014603
Other languages
English (en)
Inventor
Lin Shao
Kenneth Cooper
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.)
Texas A&M University System
Texas A&M University
Original Assignee
Texas A&M University System
Texas A&M University
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 Texas A&M University System, Texas A&M University filed Critical Texas A&M University System
Publication of WO2025171013A1 publication Critical patent/WO2025171013A1/fr
Pending legal-status Critical Current
Anticipated expiration legal-status Critical

Links

Classifications

    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C8/00—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals
    • C23C8/06—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals using gases
    • C23C8/08—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals using gases only one element being applied
    • C23C8/24—Nitriding
    • C23C8/26—Nitriding of ferrous surfaces
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C8/00—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals
    • C23C8/02—Pretreatment of the material to be coated
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C8/00—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals
    • C23C8/06—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals using gases
    • C23C8/36—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals using gases using ionised gases, e.g. ionitriding
    • C23C8/38—Treatment of ferrous surfaces
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C8/00—Solid state diffusion of only non-metal elements into metallic material surfaces; Chemical surface treatment of metallic material by reaction of the surface with a reactive gas, leaving reaction products of surface material in the coating, e.g. conversion coatings, passivation of metals
    • C23C8/80—After-treatment

Definitions

  • the present invention relates generally to the fields of molten salt reactors and metal alloy nitridation. More specifically, the present invention relates methods for nitriding a stainless steel bulk material to increase resistance to corrosion in molten salt environments.
  • Molten salt reactors are a type of advanced nuclear reactor that use a molten salt mixture as both fuel and coolant (1 ). These reactors operate at high temperatures, allowing for efficient energy production and potentially enhanced safety features compared to traditional nuclear reactors. There are no certified structural materials yet for molten salt reactors.
  • 316 SS has intergranular corrosion attack and Cr depletion in FLiBe salt, with an expected corrosion attack depth of about 16 pm for one-year service at 700°C (4).
  • This depletion is caused by the diffusion of Cr from the bulk to the near-surface grain boundary, followed by the dissolution of Cr from the grain boundaries into the salt.
  • Such dissolution is accompanied by vacancy exchange and the formation of cavities/cracks after the agglomeration of excessive vacancies.
  • corrosion leads to mass loss from the hot region and mass gain in the cold region. Such mass transfer can lead to blockage and is another materials issue, which could be even worse than corrosion itself for a molten salt reactor system.
  • Ni-based alloys have been developed for better corrosion resistance in molten salts, but these alloys face other issues, particularly with high- temperature strength (5).
  • Ni-based Hastelloy N developed at Oak Ridge National Laboratory (ORNL). It exhibits superior corrosion resistance but is not suitable for high-temperature applications. Hastelloy-N may be used for operating temperatures up to 982°C. But the maximum allowable stress for Hastelloy-N decreases dramatically for temperatures above 600°C, which is a limiting factor for usage as a structural material for reactor vessels (6).
  • Ni-based alloys are generally problematic in reactor cores due to the transmutation-induced production of helium and Co-60. Helium, generated through (n,a) reactions, can lead to embrittlement and swelling, while Co-60, a strong gamma emitter produced through neutron activation, adds significant challenges for radiation safety and waste management.
  • salts consist of LiF mixed with other fluorides. Fluoride salts have very high melting temperatures. In the accident scenario, the leaked salt would freeze and enclose radioactive fission fragments, which is one important safety benefit.
  • Two optimized salts developed over decades at ORNL are FLiBe (2LiF-BeF2) and FliNaK (46.5LiF-11.5NaF-42KF). Both have excellent thermal properties, thermochemical stability, and chemical compatibility.
  • FLiBe has an additional advantage as a fuel solvent to dissolve uranium or thorium fissile materials and is the top choice for liquid fuel. FLiNaK is excellent as coolants due to their high heat capacity.
  • Plasma-based nitridation is a low-cost, low-vacuum process, but it faces certain challenges.
  • Traditional nitridation often results in a nitrogen-strengthened phase (commonly referred to as the S-phase), where nitrogen is trapped in interstitial sites, and the steel retains its original composition and structure (7). This means the corrosion problem remains unresolved, as chromium can still leach into the salt through grain boundary diffusion.
  • S-phase nitrogen-strengthened phase
  • chromium can still leach into the salt through grain boundary diffusion.
  • nitridation may lead to the formation of a continuous nitride layer (8).
  • the structure should consist of Cr x N embedded within the steel matrix without forming a single continuous interface, thereby avoiding the challenges associated with conventional nitridation methods.
  • the invention disclosed herein addresses the alloy-related challenges in the transition from current light water reactors to the next-generation molten salt reactors.
  • the high-temperature strength alloys currently qualified for use in light water reactors suffer from corrosion issues when exposed to molten salt.
  • the corrosionresistant alloys developed for molten salt reactors fail to meet the stringent high- temperature strength requirements.
  • Applying a surface nitriding technique that forms a surface layer containing nanolayered Cr x N to immobilize chromium and to prevent its diffusion into molten salts. The technique ensures the compatibility of light water reactor alloys in molten salt environments.
  • the present invention is directed to a method for increasing corrosion resistance of a stainless steel bulk material in a molten salt environment.
  • a nanolayered composite comprising alternating layers of Cr x N and steel is formed within a surface region of the stainless steel, wherein x is 1 or 2, or, as an average, any value in between.
  • the Cr x N layers are structurally effective to immobilize chromium therein, thereby preventing its leaching into the molten salt.
  • the present invention is further directed to a nitrided stainless steel bulk material produced by the method described herein.
  • the present invention is directed to a related process further comprising cleaning the surface region of a nitrided bulk material after nitridation via mechanical removal, a chemical etchant, or a combination thereof.
  • the present invention is directed to another related process further comprising annealing a nitrided bulk material inside the nitridation chamber or outside the nitridation chamber at a temperature of about 200°C to about 1000°C for 1 second to about 1000 hours.
  • FIGS. 1A-1 B depict a molten salt reactor (FIG. 1A), where the inner surface of the steel wall contains nanolayered CrN ceramic and nanolayered steel (FIG. 1 B).
  • FIG. 2 depicts a nitridation process for the inner walls of a molten salt reactor, utilizing hollow cages to enhance the uniformity of the nitridation.
  • FIG. 3 schematically illustrates the components used during a nitridation process.
  • FIG. 4 illustrates a cathodic cage for a nitridation device with a sample placed within for surface nitridation.
  • FIGS. 5A-5D plots SEM, EDS, XRD, and indentation characterization results of nitrided 316L, obtained using a bias of 600V for 15 hours.
  • FIGS. 6A-6D plots STEM and EDS characterization results of nitrided 316L, obtained using a bias of 600V for 15 hours.
  • FIGS. 7A-7H compare STEM images of nitrided 316L steels (FIGS. 7A-7D) and untreated 316L steels (FIGS. 7E-7H) after corrosion testing.
  • the term “about” refers to a numeric value, including, for example, whole numbers, fractions, and percentages, whether or not explicitly indicated.
  • the term “about” generally refers to a range of numerical values (e.g., ⁇ 5- 10% of the recited value) that one of ordinary skill in the art would consider equivalent to the recited value (e.g., having the same function or result).
  • the term “about” may include numerical values that are rounded to the nearest significant figure.
  • a nitrided stainless steel bulk material produced by the method as described supra.
  • the nanolayered steel-Cr x N composites form within the original steel, avoiding the introduction of a separate layer or interface. This eliminates the risk of debonding at the interface, which is critical for ensuring durability in harsh reactor environments.
  • the nitridation process can be applied to modify steels for use as in-core components of molten salt reactors. Furthermore, the modified nitridation technique can be used to treat the inner surface of a vessel or a nitridation chamber wall, enabling its application as a reactor vessel in molten salt reactors.
  • 316H is a high-temperature strength alloy, suitable for working temperature up to 816°C. “H” stands for high carbon content (ranging from 0.04% to 0.10%). It can be used as reactor vessel, guard vessel, piping and heat exchangers in MSR, if corrosion issues can be resolved.
  • Chemical Processing Specific chemical processes capitalize on molten salts for their unique characteristics as reaction media or catalysts, making corrosionresistant alloys invaluable for maintaining equipment integrity.
  • the most recent example includes using molten salt as a catalyst for the synthesis of high-energy 2D material, and using molten salt as a shielding medium to synthesize oxidationresistant proton materials.
  • Metallurgy Molten salts are used in metallurgical procesing for metal refining and alloying.
  • One example is the reduction of titanium dioxide to titanium.
  • Aerospace applications such as hypersonic flight and reentry vehicles, often encounter extreme temperatures. Molten salts are employed as heat- resistant working solutions in these scenarios.
  • Molten salts have unique catalytic properties and can be utilized in the thermal processing of biomass. The processing decomposes biomasses into a mixture of liquids, non-condensable gases, and solid chars. Molten salt is simultaneously used as the heat carrier, catalyst, and solvent.
  • Molten salt has a superior capability to store heat at low cost. It is expected to play a key role in a low-carbon society. It can be used to store energy from a reactor and stabilize the electric grid by integrating solar and wind energies, which have electricity production fluctuations. Molten salt can store energy more than 30 times cheaper than lithium-ion batteries.
  • FIGS. 1A-1 B illustrate one embodiment of the corrosion-resistant molten salt reactor.
  • the reactor vessel 2 comprises the vessel wall 6, molten salt 4, a top exit pipe 8 for processing, a side exit pipe 10 for circulation, a molten salt pump 12, a heat exchanger 14, and a main bottom exit 16.
  • the dashed box highlights a small cross-sectional area of the vessel wall 6.
  • the cross-section shows the stainless steel 18 as the bulk material and a surface steel-ceramic composite layer, which includes nanolayered Cr x N 20 and nanolayered steel 22.
  • FIG. 2 illustrates a vessel 30 used as a molten salt reactor for creating the nanolayered Cr x N-steel composite on the inner surface of an MSR vessel.
  • the vessel 30 contains a vessel wall 32 made of LWR-certified steels.
  • the vessel further includes an inner hollow cage 34, which is used to produce nitrogen plasma.
  • On the wall of the hollow cage there are holes 36 designed to generate nitrogen plasma. These holes help ensure uniform plasma distribution inside the vessel.
  • Inside the hollow cage is an inner pipe 38, which is insulated from the hollow cage by insulating materials 40. On the surface of the inner pipe, it is optional to have small holes 44 that are used to release gas atoms 46 into the nitriding chamber.
  • the inner pipe is biased with a positive voltage, serving as the anode, while the hollow cage is biased negatively, acting as the cathode.
  • the vessel wall remains unbiased/floated or negatively biased. When nitrogen plasma is generated near the holes in the hollow cage, nitrogen atoms bombard the vessel wall due to its proximity to the hollow cage even when the vessel wall is floated, resulting in nitridation.
  • the vessel wall may be negatively biased to further attract nitrogen atoms if the bias voltage is appropriately selected.
  • the hollow cage is removed, and the inner pipe continues to serve as the anode, while the vessel wall becomes the cathode. In this configuration, nitrogen atoms directly bombard the vessel wall without the use of the hollow cage.
  • the anode is a pipe.
  • the pipe may be replaced with a plate of arbitrary shape.
  • nitrogen gas may be introduced into the chamber via the inner pipe.
  • nitrogen gas also may be injected into the vessel through other portals or windows. It should be noted that the vacuum pumping portal is not shown. Pumping may be conducted through portal 42 or any other suitable openings. When nitridation is required at specific temperatures, the vessel may need supplemental heating provided by a heater.
  • CCPN hollow cathode cage plasma nitriding
  • the cathode cage geometry shapes, sizes, cage thickness, and dimensions of hollow holes needs to be designed and optimized to create a high-density plasma between inner wall of the vessel, if the inner wall is to be nitrided.
  • FIG. 3 illustrates the components used in a nitriding process for a pipeline wall.
  • the pipeline wall 50 is nitrided by bombarding with N atoms.
  • the hollow cage 52 Disposed at a distance substantially close to the pipeline wall, the hollow cage 52 functions as a cathode and is biased negatively.
  • Holes 54 on the hollow cage are utilized for producing a uniform N plasma.
  • Nitrogen gas is injected into the inner pipe, which is located inside the hollow cage.
  • the inner pipe 56 functions as an anode and is biased positively.
  • Holes 58 on the inner tube surface are utilized for releasing N atoms, which are injected into the chamber through the inner tube.
  • the inner tube is insulated from the hollow cage by insulating materials 60. The assembly of the hollow cage and the inner tube rotates during the nitridation process, which further improves the uniformity of nitridation on the pipeline wall.
  • FIG. 4 shows the cross-sectional scanning electron microscopy (SEM) images of the nitrided 316L SS along with the corresponding Energy-Dispersive X-ray Spectroscopy (EDS) mapping.
  • SEM scanning electron microscopy
  • Nitriding modifies the surface up to a depth of 60 microns, evident from the image contrast (FIG. 5A). Within this region, N is enriched, Fe is reduced, while chromium is unchanged. No oxides or oxide precipitates are observed. EDS line scan suggests the formation of Cr x N (FIG. 5B). X-ray diffraction analysis (XRD) analysis observes the characteristic peaks of Cr x N (FIG. 5C). Cross sectional indentation mapping shows that the nitride layer exhibits significantly enhanced hardness, increased by a factor of about three (FIG. 5D).
  • XRD X-ray diffraction analysis
  • the nitrided region displays distinctive nanometer-scale patterns, with alternating arrangements of Fe-enriched phase and Cr x N phases in a lamellar structure (as shown in FIG. 6A).
  • the spacing between adjacent Fe layers measures approximately 50 nm.
  • SEM mapping reveals a correlated spatial distribution of Cr and N.
  • Fe and Ni exhibit enrichment between adjacent Cr x N layers (as shown in FIG. 6B).
  • the EDS line scan shows the periodic formation of nanolayers with a Cr- to-N ratio close to 1 :1 (FIG. 6C).
  • FIG. 6D an FFT (Fast Fourier Transform) filtered STEM image of the Cr x N phase is presented.
  • the interplanar spacing of the (200) plane of the nitride is 2.11 A, which corresponds to a lattice parameter of 4.22 A, aligning well with the literature-reported value for Cr x N.
  • Fe-enriched phase and Cr x N lamellar structures is believed to be the decomposition product of metastable nitrogen-expanded austenite.
  • Low-temperature nitriding ( ⁇ 450°C) of 316 SS ends with nitrogen- expanded austenite, the so-called S phase in literature, while high-temperature nitridation (> ⁇ 450°C) ends with a Cr x N-containing compound layer.
  • a temperature higher than 500°C may result in y-Fe, based on the Cr-N phase diagram.
  • the nitrided sample exhibits significantly enhanced corrosion resistance in FLiNaK. No microcracks were observed from either cross-sectional or planar SEM images (FIGS. 7E, 7G). Chromium distribution is homogeneous in both the cross- sectional and planar EDS mapping (FIGS. 7F, 7H). Homogeneous elemental distributions are also observed for other elements such as Fe and N. There is no evidence that N is lost during the 700°C corrosion testing, as judged by the yield before and after corrosion testing, which is expected from the strong Cr x N bonding.
  • the ambient atmosphere consists of 90% nitrogen and 10% hydrogen (H).
  • H hydrogen
  • the choice of cage materials in the CCPN setup matches those of the substrates to be nitrided.
  • the substrate temperature is determined by the plasma flux and the bias applied between the anode and cathode. The bombarding energies of N atoms on the substrate greatly influence the thermal energy transferred to the substrate. Consequently, in a typical CCPN process, the substrate temperature is primarily influenced by the voltage bias.
  • the nitridation process requires optimizing a range of biases and chamber pressures to facilitate nitriding without causing deposition of cage materials to the substrate.
  • a first method is to avoid the use of a hollow cage.
  • a second method is to apply plasma sputtering after the nitridation process. This can easily be achieved by switching from nitrogen plasma nitridation to argon plasma sputtering. As a heavy atom, argon is highly efficient for surface sputtering. Careful control of the argon plasma treatment time can effectively remove any surface contaminant layer that may form during the nitridation step.
  • a third method involves surface polishing or etching. This is accomplished by using mechanical polishing with materials such as SiC paper or alumina oxide paper.
  • the surface contaminant layer is relatively easy to remove. However, once etching reaches the nanostructured layer beneath the contaminant layer, the etching rate drops significantly due to the high hardness of the nanolayered region.

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  • Chemical & Material Sciences (AREA)
  • Chemical Kinetics & Catalysis (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Solid-Phase Diffusion Into Metallic Material Surfaces (AREA)

Abstract

L'invention concerne des procédés pour augmenter la résistance à la corrosion d'acier inoxydable dans des environnements de sel fondu. Un matériau en vrac ayant une structure nanostratifiée de couches alternées de CrxN et de l'acier inoxydable est formé à l'intérieur d'une région de surface de celui-ci par nitruration au plasma. Dans les couches de CrxN, x vaut 1, 2 ou, en moyenne, toute valeur comprise entre ces valeurs. L'invention concerne également le matériau en vrac ayant une résistance à la corrosion accrue dans un environnement de sel fondu formé par la nitruration au plasma.
PCT/US2025/014603 2024-02-08 2025-02-05 Procédé de modification de surface d'aciers inoxydables utilisés dans des environnements de sel fondu Pending WO2025171013A1 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
US202463551407P 2024-02-08 2024-02-08
US63/551,407 2024-02-08

Publications (1)

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WO2025171013A1 true WO2025171013A1 (fr) 2025-08-14

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Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP0008228A2 (fr) * 1978-08-14 1980-02-20 The Garrett Corporation Aciers inoxydables ferritiques nitrurés intérieurement et procédés d'obtention de ces aciers
US20090123737A1 (en) * 2006-01-18 2009-05-14 Toyoaki Yasui Solid Particle Erosion Resistant Surface Treated Coat and Rotating Machine Applied Therewith
CN106148904A (zh) * 2015-04-17 2016-11-23 中国科学院金属研究所 一种纳米叠层CrN镀膜及其制备方法和应用
CN108950548A (zh) * 2018-08-10 2018-12-07 成都极星等离子科技有限公司 铬-氮化铬复合涂层及其在纳米复合刀具的应用
US11168392B2 (en) * 2015-05-26 2021-11-09 Oerlikon Surface Solutions Ag, Pfähhikon Wear and/or friction reduction by using molybdenum nitride based coatings

Patent Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP0008228A2 (fr) * 1978-08-14 1980-02-20 The Garrett Corporation Aciers inoxydables ferritiques nitrurés intérieurement et procédés d'obtention de ces aciers
US20090123737A1 (en) * 2006-01-18 2009-05-14 Toyoaki Yasui Solid Particle Erosion Resistant Surface Treated Coat and Rotating Machine Applied Therewith
CN106148904A (zh) * 2015-04-17 2016-11-23 中国科学院金属研究所 一种纳米叠层CrN镀膜及其制备方法和应用
US11168392B2 (en) * 2015-05-26 2021-11-09 Oerlikon Surface Solutions Ag, Pfähhikon Wear and/or friction reduction by using molybdenum nitride based coatings
CN108950548A (zh) * 2018-08-10 2018-12-07 成都极星等离子科技有限公司 铬-氮化铬复合涂层及其在纳米复合刀具的应用

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