CN102428200B - High strength/corrosion-resistant austenitic stainless steel with carbon - nitrogen complex additive, and method for manufacturing same - Google Patents
High strength/corrosion-resistant austenitic stainless steel with carbon - nitrogen complex additive, and method for manufacturing same Download PDFInfo
- Publication number
- CN102428200B CN102428200B CN200980159318.1A CN200980159318A CN102428200B CN 102428200 B CN102428200 B CN 102428200B CN 200980159318 A CN200980159318 A CN 200980159318A CN 102428200 B CN102428200 B CN 102428200B
- Authority
- CN
- China
- Prior art keywords
- stainless steel
- austenitic stainless
- nitrogen
- content
- alloy
- 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.)
- Active
Links
Images
Classifications
-
- 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
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
-
- 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
- C21D6/002—Heat treatment of ferrous alloys containing Cr
-
- 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
- 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
- C21D8/021—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips involving a particular fabrication or treatment of ingot or slab
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0226—Hot rolling
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- 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
- C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
- C21D8/0405—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing of ferrous alloys
-
- 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
- C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
- C21D8/041—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing involving a particular fabrication or treatment of ingot or slab
-
- 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
- C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
- C21D8/0421—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the working steps
- C21D8/0426—Hot rolling
-
- 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
- C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium 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
- C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of 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
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/001—Austenite
Abstract
The present invention relates to high strength/corrosion-resistant austenitic stainless steel with a carbon-nitrogen complex additive, and particularly, to an austenitic stainless steel with a carbon (C) and nitrogen (N) complex additive containing: 8-12 wt % of manganese (Mn); 15-20 wt % of chromium (Cr); less than 2 wt % of nickel (Ni); less than 4 wt % of tungsten (W); less than 2 wt % of molybdenum (Mo); 0.6-1.0 wt % of the total content (C+N) of carbon (C) and nitrogen (N); with the remainder being iron (Fe) and other unavoidable impurities, and to a method for manufacturing same. By controlling the content of the interstitial elements (C+N, C/N) and the substitution elements (Mn+Cr, Mn/Cr, or 0.5W+Mo), the austenitic stainless steel manufactured according to the present invention has a tensile strength of more than 850 MPa and uniform elongation of more than around 45%, thereby exhibiting excellent corrosion resistance as well as improving processability, and the content of Ni, a toxic alloy element, is minimized to improve biocompatibility, making the austenite stainless steel applicable to conventional and offshore structures, desalination facilities, and materials for oil and gas facilities / drilling, transportation and the like, which require high strength and high corrosion resistance, and may also be used to manufacture various functional parts for medical prosthetic materials, and accessories such as jewelry, watches, and the like.
Description
Technical field
The present invention relates to have C+N austenitic stainless steel and the manufacture method thereof of high mechanical strength and good corrosion.
Background technology
Conventionally, with the mechanical property of carbon steel, such as intensity and ductility, can be processed or be improved difference by various heat treated phase transformations by thermomechanical, the mechanical property of using heat treating method to improve austenitic stainless steel be difficult.Thereby austenitic stainless steel mainly relies on interpolation alloying element and improves most of performance.
Therefore, in the exploitation of novel alloy, most important technical problem is in the situation that by minimizing the content of high price alloying element or reducing manufacturing cost by substitute high price alloying element with economical alloying element, guarantee to comprise that the performance of intensity, ductility or erosion resistance is best.
Chromium (Cr), the nickel (Ni) of 6～12wt.%, the carbon (C) of the molybdenum (Mo) of 0～2wt.% and 0.03～0.15wt.% that in former research or invention, most of austenitic stainless steels of report contain 16～20wt.%, and present the tensile strength of 500～600MPa and 40% unit elongation.
In above-mentioned alloying element, nickel (Ni) is effective austenite stabilizer element, and it contributes to improve forging property.More than 65% nickel (Ni) of aggregate supply is consumed for producing austenitic stainless steel.
Yet, from calendar year 2001 in subsequently 6 years the price continuous rise of nickel (Ni) more than 700%, especially, in the time of 2007, price is double, therefore, the price of nickel (Ni) has become the leading indicator that determines stainless steel price.Except economic angle, because nickel (Ni) can cause anaphylaxis and discharge poisonous gas in process recycling human skin, therefore, nickel (Ni) also can cause side effect to HUMAN HEALTH and environment.
Thereby, in order to solve the problem relevant to the traditional stainless steel that contains high content nickel (Ni), developed Fe-Cr-Mn alloy (or STS 200 alloys), and owing to adding nitrogen (N) and have the high-nitrogen austenitic stainless steel of desirable physical and chemical performance.
Nitrogen (N) is very effective austenite stabilizer element, has a plurality of advantages, and this advantage comprises ductility that solid solution hardening, physical strength increase the follow erosion resistance less and that improve that declines.Owing to being difficult to guarantee the nitrogen (N) of high-content in steel in manufacturing processed, therefore high nitrogen stainless steel does not also have commercialization up to now.Recently, carried out multiple research and developed effective manufacture method, result, pressurized Induction Melting, high pressure esr (PESR), powder metallurgy and under nitrogen atmosphere solution nitriding be proposed.
Yet the business-like major obstacle of high nitrogen stainless steel is the special manufacture processing units of requirement, such as pressurized Induction Melting stove or PESR, this requires expensive equipment and complicated treatment step.
Pressure treatment is especially essential to manufacturing the large size ingot casting of high nitrogen stainless steel, this is because pressure treatment can be guaranteed to have in liquid metal the nitrogen (N) of high-content and can minimize delta ferrite gap, and this delta ferrite gap can significantly reduce nitrogen (N) solubleness at solidificating period.Thereby, improve traditional melting equipment or in pressure process, introduce new equipment being inevitable for adopting pressurization melting equipment to manufacture high nitrogen stainless steel, therefore, high nitrogen stainless steel is not also by commercialization.
Recently, the people such as H.Berns disclose austenitic steel in international patent application no PCT/EP2005/008960, the molybdenum (Mo) of the chromium (Cr) that it contains minimum nickel (Ni), 16～21wt.%, the manganese (Mn) of 16～21wt.%, 0.5～2wt.% and 0.8wt.% or the more carbon of volume (C) and nitrogen (N) ([C+N]), as the proposal that solves the problem in above-mentioned manufacturing processed.Yet, the manganese (Mn) that people's inventions disclosed such as H.Berns comprise relative high-content, it has reduced erosion resistance subsequently.
The inventor has has researched and developed and has manufactured the C+N austenitic stainless steel of economic benefit, high strength and the good corrosion with raising, wherein added carbon (C) and nitrogen (N) simultaneously but not nickel (Ni) as interstitial element.Therefore, the content of high price nickel (Ni) can be reduced to minimum, and by controlling the content of two kinds of interstitial element carbon (C) and nitrogen (N) (C+N, C/N) and those substitutional element manganese (Mn), chromium (Cr), molybdenum (Mo) and tungsten (W) (Mn+Cr, Mn/Cr or 0.5W+Mo), intensity and corrosion resistance access raising.In addition, this alloy is compared and is more had economic competitiveness with traditional high nitrogen stainless steel, and this is because it can be produced by the traditional smelting furnace except pressure process.
Summary of the invention
One aspect of the present invention is to address the above problem, thereby, the object of the invention is to provide by the content of control gap element (C+N, C/N) and substitutional element (Mn+Cr, Mn/Cr or 0.5W+Mo) the C+N austenitic stainless steel of intensity and the good corrosion with raising.
Another object of the present invention is to provide the manufacture method of above-mentioned austenitic stainless steel.
In one embodiment, provide C+N austenitic stainless steel, added wherein carbon (C) and nitrogen (N) as interstitial element simultaneously, therefore, the content of nickel (Ni) is minimized, and nickel is the alloying element of high price, harmful to environmental and human health impacts.As a result, the austenitic stainless steel of formation provides improved economic benefit.
Use can be manufactured the alloy with economic production cost according to the manufacture method of one embodiment of the invention, and therefore can put forward heavy alloyed price competitiveness.And, according to the austenitic stainless steel of an embodiment, have good mechanical property (tensile strength is higher than 850MPa) and uniform elongation (higher than 45%), its content by control gap element (C+N, C/N) and substitutional element (Mn+Cr, Mn/Cr or 0.5W+Mo) obtains.In addition,, due to the nickel (Ni) (nickel can cause anaphylaxis to human body) of high alloy nitrogen (N) and minimum content, alloy of the present invention also shows good erosion resistance and biocompatibility.Therefore, the manufacture of various functional modules, wrist-watch and the annex that can effectively be applied to according to austenitic stainless steel of the present invention to comprise medico's material (medical biosubstance), and the austenitic stainless steel and the off-shore structure field that require the traditional structure of high level intensity and erosion resistance, Desalination plants, the material of installing/gathering for oil gas, and for the material of transportation equipment.
Accompanying drawing explanation
By reference to accompanying drawing, some exemplary is described, above and/or other aspects described herein will become clearer, wherein:
Fig. 1 is nitrogen (N) solubleness as the variation diagram of the function of Fe-Cr-Mn base alloy and Fe-Cr-Mn-0.4C base alloy temperature according to embodiments of the present invention;
Fig. 2 is the schema according to embodiments of the present invention with the C+N austenitic stainless steel preparation method of high mechanical strength and good corrosion;
Fig. 3 is that details drawing is shown in the schema that regulates the 4th step of nitrogen (N) content in the C+N austenitic stainless steel preparation process according to embodiments of the present invention with high mechanical strength and good corrosion; And
Fig. 4 is the contrast diagram of pitting corrosion between the embodiment of the present invention and comparative example.
* the description * of the main reference number of Fig. 2 and Fig. 3
Embodiment
Referring now to accompanying drawing, some exemplary is described in more detail.
According to an embodiment, there is the C+N austenitic stainless steel of high strength and good corrosion by forming below: 8 to 12wt.% manganese (Mn); 15 to 20wt.% chromium (Cr); 2wt.% or nickel still less (Ni); 4wt.% or tungsten still less (W); 2wt.% or molybdenum still less (Mo); 0.6 to 1.0wt.% C+N content; The iron of equal amount (Fe); And inevitable impurity.
Manganese (Mn) is 0.5 to 1.0 with the ratio (Mn/Cr) of chromium (Cr).
According to an embodiment, because the content of manganese in the present invention (Mn) is lower than the content (i.e. 16 to 21wt.% manganese (Mn)) of the disclosed stainless manganese of people such as H.Berns in international patent application no PCT/EP2005/008960, therefore, obtained improved pitting corrosion.
The total content of manganese (Mn) and chromium (Cr) ([Mn+Cr]) is 30wt.% or still less.
Nitrogen (N) content is 0.3wt.% or more.
The total content (0.5W+Mo) of tungsten (W) and molybdenum (Mo) is 3wt.% or lower.If 0.5W+Mo content surpasses 3wt.%, manufacturing cost increases, and the amount of residual delta ferrite raises, and forms harmful second-phase.
The alloying element of austenitic stainless steel according to embodiments of the present invention will be described in detail below.
Although the effective stable austenite phase of nickel (Ni) meeting, considers high price and the side effect to environmental and human health impacts, nickel (Ni) content is limited in low as far as possible.Yet, consider to add in austenitic stainless steel micro-nickel (Ni) can improve heat and/cold formability, and suppress solidificating period delta ferrite and form from liquid phase, the interpolation of nickel (Ni) is limited in 2wt.%.
Chromium (Cr) is the essential alloying element of guaranteeing stainless steel erosion resistance, and most of austenitic stainless steel comprises 15wt.% or more chromium (Cr).Yet excessive interpolation chromium (Cr) can cause the delta ferrite that solidifies the residual surplus of rear formation, and promote the various second-phase precipitations of during Heat Treatment, this has weakened stainless erosion resistance and plasticity.Therefore,, in stainless steel, chromium (Cr) content is limited in 15～20wt.%.
Manganese (Mn) is austenite stabilizer element, and it can replace the nickel (Ni) of high price.In addition, when adding in stainless steel, manganese (Mn) can improve the solubleness of nitrogen (N), and thereby improves the physical strength of material.Yet the manganese of excessive interpolation (Mn) combines with sulphur (S) or oxygen (O) in stainless steel base conventionally, form non-metallic inclusion, such as manganese sulfide (MnS) or manganese oxide (MnO).Non-metallic inclusion is as the initiation site of pitting attack, thereby they can weaken the pitting corrosion of austenitic stainless steel.Therefore, manganese (Mn) content is limited in 8～12wt.%.
Similar to chromium (Cr), molybdenum (Mo) also can improve the erosion resistance of austenitic stainless steel.Yet the molybdenum of excessive interpolation (Mo) also can increase the amount of solidifying rear residual delta ferrite, and similar to chromium (Cr), can bring out and form harmful second-phase.In addition, add a large amount of Mo can increase manufacturing cost.Therefore, molybdenum (Mo) content is limited in 2wt.% or still less.
Tungsten (W) can effectively replace molybdenum (Mo), and this is the ability that has stable ferritic phase and improve pitting corrosion because of tungsten (W), is equivalent to 1/2 equivalent of molybdenum (Mo) content.In addition, tungsten (W) can increase stainless hot strength and creep resistance.Equally, tungsten (W) can improve general erosion resistance in non-oxidizing atmosphere, promotes metal passivation, and improves the pitting corrosion of alloy.Yet as ferrite stabilizer, in stainless steel, the tungsten of excessive existence (W) can increase the amount of delta ferrite, and also meeting similar to molybdenum (Mo) improves manufacturing cost.Therefore, tungsten (W) content is limited in 4wt.% or still less.In addition,, in order to obtain high erosion resistance and economic manufacturing cost, 0.5W+Mo content is limited in 3wt.% or still less.
Nitrogen (N) adds as austenite stabilizer element together with carbon (C) and manganese (Mn), to replace the nickel (Ni) that has the problems referred to above, and in the situation that not causing perceptible ductility to decline, improve intensity, and promotion comprises the erosion resistance of pitting corrosion.Thereby the nitrogen of 0.3wt.% or more high-content (N) has been used as this kind of effect.Yet excessive nitrogen (N) can cause the reduction of ductility and ductility to the transformation of fragility.
Similar to nitrogen (N), add carbon (C) with stable austenite phase, and improve stainless physical strength by solid solution hardening.Yet excessive C can reduce toughness, at crystal boundary, form carbide, such as M
23c
6or M
6c, this makes crystal boundary sensitization, causes erosion resistance to decline.
Because these reasons, are limited in 0.6～1.0wt.% at the total content ([C+N]) according to carbon (C) in the stainless steel of embodiment of the present invention and nitrogen (N).
Simultaneously, it is under 1atm that Fig. 1 illustrates nitrogen partial pressure, not the Fe-Cr-Mn base ternary alloy of carbon containing (C) (being Fe-18Cr-10Mn, Fe-15Cr15Mn and Fe-13Cr-20Mn alloy) and containing the result of nitrogen (N) solubleness calculating in the Fe-Cr-Mn-0.4C base ternary alloy of 0.4wt.% carbon (C).Referring to Fig. 1, by adding carbon (C), nitrogen in liquid metal (N) solubleness is reduced to 0.3wt.% from 0.38wt.%.Yet, because form at solidificating period delta ferrite nitrogen (N) the solubleness decline causing that declines by adding carbon (C), obviously suppressed, so can reduce the loss of alloy nitrogen (N).This phenomenon is owing to causing by the increase of austenite phase stability and ferritic phase stability decreases under interpolation carbon (C) high temperature.Based on this cognition, when carbon (C) and nitrogen (N) are added in stainless steel base simultaneously, can obtain the solubleness of target nitrogen (N) under normal atmosphere (being that nitrogen partial pressure is under 1atm).
In addition, below will explain carbon (C) and nitrogen (N) content (C+N) will be limited to the reason within the scope of 0.6～1.0wt.%.The nitrogen (N) of interpolation can increase the free electron density of austenitic matrix, and it transfers to promote metal link character and strengthen the short range order distribution (short-range ordering) in austenitic matrix.Due to by adding this kind of characteristic atomic bonding of nitrogen (N) induction, can limit by the segregation of alloying element the generation of harmful second-phase, and thereby improve ductility and erosion resistance.In other words, the physical basis that improves the general property of steel by adding nitrogen (N) can find from the increase of free electron density.On the other hand, different from the nitrogen (N) of predetermined content scope, add carbon (C) free electron density of steel is not produced to obvious impact.Yet if combine interpolation carbon (C) and nitrogen (N) in stainless steel base, due to the synergy between two elements, with the alloy phase ratio that only adds nitrogen (N), stainless steel will present very high free electron density.Free electron density increases gradually with the content ([C+N]) of carbon (C) and nitrogen (N), at [C+N], reaches maximum value during for 0.85wt.%, after this starts to decline.Therefore,, based on above-mentioned physical basis, also, in order to prevent from causing due to excessive interpolation carbon (C) and nitrogen (N) generation of unwanted secondary sedimentation phase, according to the total C+N content of one embodiment of the invention, be limited in 0.6～1.0wt.%.
In addition, the manufacture method with the C+N austenitic stainless steel of high strength and good corrosion according to the present invention comprises the steps: S100: mother alloy feeds intake, wherein mother alloy is dropped in vacuum melting furnace, the chemical constitution of mother alloy is (all by weight percentage) pure iron, Fe-50%Mn, Fe-60%Cr, Fe-58.8%Cr-6.6%N, 75.1%Mn-17.4%Fe-6.8%C, tungsten (W) and/or molybdenum (Mo); S200: maintain vacuum, wherein throwing is had the vacuum melting furnace of mother alloy to maintain under vacuum; S300: master alloy melting, wherein heating, vacuum smelting furnace master alloy melting; S400: regulate nitrogen (N) content, wherein nitrogen is injected to vacuum melting furnace; S500: the alloy of stir-melting, the wherein mother alloy of stir-melting; S600: form ingot casting, wherein form ingot casting by pour into a mould the alloy of melting from vacuum melting furnace; S700: the ingot casting that hot rolling forms; And S800: the stainless steel of hot rolling is carried out to water quenching, and to prevent carbide precipitation, this carbide can adversely affect mechanical property and erosion resistance.
The step (S200) that maintains vacuum is that the vacuum level in vacuum melting furnace is maintained to 10
-3holder or lower step.
Regulate the step (S400) of N content to comprise two steps: nitrogen injection (S420), wherein injects vacuum melting furnace by nitrogen; And regulate pressure (S440), wherein the dividing potential drop of nitrogen in vacuum melting furnace is adjusted to 1atm.
Embodiment of the present invention can be applicable to manufacture the austenitic stainless steel with high strength and good corrosion, and various forms of stainless steels comprise casting, forging and the rolling stainless steel with economic manufacturing cost and raw materials cost.
According to the austenitic stainless steel of one embodiment of the invention, there is 850MPa or higher tensile strength and 45% or higher Uniform Tension rate (in Table 2).And, according to the good erosion resistance of the austenitic stainless steel of one embodiment of the invention, by measuring potential scanning speed (dV/dt), at the 1M NaCl of 2mV/s place solution Anodic polarization behavior, determine.
Therefore,, according to embodiment of the present invention, the austenitic stainless steel that contains carbon (C) and nitrogen (N) can be manufactured by the atmosphere induction melting technique except pressure treatment (it is essential in the classical production process of high nitrogen steel).Because can manufacture the alloy with economic manufacturing cost, so the price competitiveness of exploitation alloy has increased.In addition, by the content of control gap element (C+N, C/N) and the content of substitutional element (Mn+Cr, Mn/Cr or 0.5W+Mo), successfully obtain high tensile strength (850MPa or higher) and guaranteed the good Uniform Tension rate (45% or higher) of plasticity, and improved erosion resistance.In addition, because minimized the content of harmful nickel (Ni), therefore, according to austenitic stainless steel of the present invention, not only can effectively be applied to require austenitic stainless steel and the off-shore structure field of the traditional structure of high-level physical strength and erosion resistance, Desalination plants, the material of installing/gathering for oil gas, and for the material of transportation equipment; And the manufacture of various functional modules, wrist-watch and the annex that can effectively be applied to comprise medico's material.
Below will explain in more detail exemplary of the present invention and example.Yet, should be appreciated that, the embodiment of explaining and example are only for task of explanation, and therefore, aim of the present invention is not subject to the restriction of exemplary.
Embodiment 1 to 8: austenitic stainless steel constructed in accordance
According to embodiment of the present invention, in manufacturing austenitic stainless steel, ferrochrome mother alloy (for example, Fe-60%Cr mother alloy) is as chromium source, and due to high fusing point, it melts hardly; Ferromanganese mother alloy (for example, Fe-50%Mn mother alloy) is as manganese (Mn) source, to prevent manganese (Mn) cigarette and because low-steam pressure causes segregation in smelting metal.
Referring to Fig. 2 and 3, in step S100, by by Fe-50%Mn, Fe-60%Cr, pure iron, for control nitrogen (N) content Fe-58.8%Cr-6.6%N, for controlling the mother alloy that 75.1%Mn-17.4%Fe-6.8%C, tungsten (W) and/or the molybdenum (Mo) of carbon (C) content form, drop into vacuum melting furnace.In step S200, vacuum melting furnace is degassed, until vacuum level becomes 10
-3holder or following, maintains this vacuum level.In step S300, heating, vacuum smelting furnace, so that abundant master alloy melting and pure iron.In step S400, by nitrogen being introduced to vacuum melting furnace (in step S420) when master alloy melting and the pure iron and by the interior dividing potential drop of nitrogen being adjusted between smelting period to the content that 1atm (in step S440) regulates nitrogen (N).In step S500, by the alloy of electromagnetic induction stirring action stir-melting, to avoid the segregation of alloying element.In step S600, when the mother alloy metal of melting during whipping step S500 and the temperature of pure iron reach 1450 ℃, by forming ingot casting from vacuum melting furnace cast molten alloy.In step S700, by hot rolling, to manufacture the ingot casting of the forms such as plate, pipe, rod, silk, and in step S800, carry out water quenching processing to prevent carbide precipitation, this carbide can reduce mechanical property and erosion resistance conventionally.
Comparative example 1 to 3: business austenitic stainless steel
The austenitic stainless steel that use is purchased (being AISI 304, AISI 316, AISI 316L).
Comparative example 4 and 5
According to preparing austenitic stainless steel disclosed composition by people such as H.Berns in number of patent application PCT/EP2005/008960.
The composition of embodiment and comparative example's austenitic stainless steel is listed in table 1.
Table 1 (wt.%)
| Alloy | Cr | Mn | Ni | Mo | W | N | C | C+N |
| Embodiment 1 | 18.10 | 9.47 | - | 2.17 | - | 0.38 | 0.48 | 0.86 |
| Embodiment 2 | 17.85 | 9.72 | 1.25 | 2.05 | - | 0.42 | 0.49 | 0.91 |
| Embodiment 3 | 17.98 | 9.79 | - | - | 2.01 | 0.39 | 0.48 | 0.87 |
| Embodiment 4 | 17.71 | 9.85 | 1.21 | - | 2.00 | 0.36 | 0.55 | 0.91 |
| |
18.12 | 9.63 | 0.10 | 1.16 | 2.00 | 0.38 | 0.53 | 0.91 |
| Embodiment 6 | 17.73 | 9.97 | 1.23 | 1.15 | 1.99 | 0.39 | 0.52 | 0.91 |
| Embodiment 7 | 17.68 | 9.84 | - | - | 3.80 | 0.41 | 0.56 | 0.97 |
| Embodiment 8 | 17.65 | 9.73 | 1.17 | - | 3.77 | 0.43 | 0.54 | 0.97 |
| Comparative example 1 | 18.00 | 2.00 | 8.00 | - | - | - | 0.08 | 0.08 |
| Comparative example 2 | 17.00 | 2.00 | 12.00 | 2.50 | - | - | 0.08 | 0.08 |
| Comparative example 3 | 17.00 | 2.00 | 12.00 | 2.50 | - | - | 0.03 | 0.03 |
| Comparative example 4 | 18.54 | 17.86 | 0.45 | 0.52 | - | 0.54 | 0.66 | 1.20 |
| Comparative example 5 | 17.97 | 17.8 | 0.36 | 0.51 | - | 0.58 | 0.48 | 1.06 |
Experiment 1: the measurement of tensile property
The embodiment manufacturing according to an embodiment of the present invention and comparative example's tensile property are listed in table 2.
Table 2
As shown in table 2, be that 170～205MPa, tensile strength are that the business austenitic stainless steel that 480～515MPa, extensibility are 40% is compared with comparative example's 1 to 3 yield strength, embodiment constructed in accordance shows better mechanical property, yield strength is 476～559MPa, tensile strength is 868～980MPa, and Uniform Tension rate is 46.3～62.1%.
And, the disclosed C+N austenitic stainless steel of people (comparative example 4 and the comparative example 5) mechanical propertys such as embodiment constructed in accordance and H.Berns are suitable, and yield strength is that 500～533MPa, tensile strength are that 940～1019MPa, Uniform Tension rate are 59.0～62.8%.
Therefore, austenitic stainless steel minimizes nickel (Ni) content according to embodiments of the present invention, and compares with business austenitic stainless steel, presents superior mechanical property.Therefore, according to austenitic stainless steel of the present invention, can replace traditional austenitic stainless steel.
Experiment 2: the measurement of erosion resistance
In order to measure the erosion resistance according to austenitic stainless steel of the present invention, observed the anodic polarization performance of sample, result, has measured pitting attack current potential.To at room temperature immerse in 1M NaCl solution according to the embodiment of the present invention and comparative example's austenite stainless steel sample, with potential scanning speed (dV/dt) the raising current potential of 2mV/s.As shown in Figure 4, the some current potential recording is listed in table 3 to polarization response.
Table 3
| Alloy | Point current potential (E Point)、V SCE |
| Embodiment 1 | Without pitting attack (1.0 or more than) |
| Embodiment 2 | Without pitting attack (1.0 or more than) |
| Embodiment 3 | Without pitting attack (1.0 or more than) |
| Embodiment 4 | Without pitting attack (1.0 or more than) |
| |
Without pitting attack (1.0 or more than) |
| Embodiment 6 | Without pitting attack (1.0 or more than) |
| |
Without pitting attack (1.0 or more than) |
| Embodiment 8 | Without pitting attack (1.0 or more than) |
| Comparative example 1 | 0.311 |
| Comparative example 2 | 0.417 |
| Comparative example 3 | 0.496 |
| Comparative example 4 | 0.557 |
| Comparative example 5 | 0.692 |
As shown in Fig. 4 and table 3, according to embodiments of the invention 1 to 8, there is no appearance point corrosion.On the contrary, for comparative example 1 to 3 business stainless steel, pitting attack occurs in 0.311～0.496V
sCEplace, for traditional C+N stainless steel of comparative example 4 and 5, pitting attack occurs in 0.557～0.692V
sCEplace.Therefore, obviously, compare with comparative example, the austenitic stainless steel of manufacturing according to an embodiment of the present invention has superior pitting corrosion.
Therefore, compare with business austenitic stainless steel or traditional C+N austenitic stainless steel, austenitic stainless steel has the nickel (Ni) of minimum content according to embodiments of the present invention, presents superior mechanical property and the erosion resistance of raising.Therefore, according to austenitic stainless steel of the present invention, can replace traditional austenitic stainless steel.
Aforementioned exemplary embodiment and advantage are only exemplary, are not interpreted as limiting the present invention's design.This instruction can easily be applied to the device of other types.Equally, the description object of illustrative embodiments of the invention is illustrative, does not limit claimed scope, and to those skilled in the art, many replacements, modification and variation will be apparent.
Claims (11)
1. a C+N austenitic stainless steel with high mechanical strength and good corrosion, it is by 8 to 12wt.% manganese (Mn); 15 to 20wt.% chromium (Cr); 2wt.% or nickel still less (Ni); Total C+N content of 0.6 to 1.0wt.%; 4wt.% or tungsten still less (W); 2wt.% or molybdenum still less (Mo); The iron of equal amount (Fe); And inevitably impurity forms,
Wherein, manganese (Mn) is 0.5 to 1.0 with the ratio (Mn/Cr) of chromium (Cr), and
Wherein, the mechanical property of described C+N austenitic stainless steel comprises 850MPa at room temperature or higher tensile strength and 45% or higher Uniform Tension rate.
2. C+N austenitic stainless steel according to claim 1, it is by 8 to 12wt.% manganese (Mn); 15 to 20wt.% chromium (Cr); 2wt.% or nickel still less (Ni); 1 to 4wt.% tungsten (W); Total C+N content of 0.6 to 1.0wt.%; The iron of equal amount (Fe); And inevitably impurity forms.
3. C+N austenitic stainless steel according to claim 1, it is by 8 to 12wt.% manganese (Mn); 15 to 20wt.% chromium (Cr); 2wt.% or nickel still less (Ni); 2wt.% or molybdenum still less (Mo); Total C+N content of 0.6 to 1.0wt.%; The iron of equal amount (Fe); And inevitably impurity forms.
4. C+N austenitic stainless steel according to claim 1, it is by 8 to 12wt.% manganese (Mn); 15 to 20wt.% chromium (Cr); 2wt.% or nickel still less (Ni); 1 to 4wt.% tungsten (W); 2wt.% or molybdenum still less (Mo); Total C+N content of 0.6 to 1.0wt.%; The iron of equal amount (Fe); And inevitably impurity forms.
5. C+N austenitic stainless steel according to claim 1, wherein the total content ([Mn+Cr]) of manganese (Mn) and chromium (Cr) is 30wt.% or still less.
6. C+N austenitic stainless steel according to claim 1, wherein nitrogen (N) content is 0.3wt.% or more.
7. C+N austenitic stainless steel according to claim 1, wherein the total content (0.5W+Mo) of tungsten (W) and molybdenum (Mo) is 3wt.% or lower.
8. a manufacture method with the C+N austenitic stainless steel of high mechanical strength and good corrosion according to claim 1, described manufacture method is comprised of following steps:
The mother alloy that feeds intake, wherein drops into mother alloy in vacuum melting furnace;
Maintain vacuum, wherein will throw and have the described vacuum melting furnace of described mother alloy to maintain under vacuum wherein;
Master alloy melting, wherein heats mother alloy described in described vacuum melting furnace melting;
Regulate nitrogen (N) content, wherein nitrogen is injected to described vacuum melting furnace;
The alloy of stir-melting, the wherein mother alloy of stir-melting;
Form ingot casting, wherein the alloy by the melting that cast is stirred from described vacuum melting furnace forms ingot casting;
The ingot casting forming described in hot rolling; And
The stainless steel of hot rolling is carried out to water quenching, and to prevent carbide precipitation, described carbide reduces mechanical property and erosion resistance.
9. manufacture method according to claim 8, in the described step that maintains vacuum, maintains 10 by the vacuum level in described vacuum melting furnace
-3holder or lower.
10. manufacture method according to claim 8, wherein regulates nitrogen (N) content to comprise:
Nitrogen injection, wherein injects nitrogen the inside of described vacuum melting furnace; And
Regulate pressure, wherein the dividing potential drop of the nitrogen of described vacuum melting furnace interior is adjusted to 1atm.
11. C+N austenitic stainless steels according to claim 1, wherein said C+N austenitic stainless steel is by being manufactured by the method forming below:
The mother alloy that feeds intake, wherein drops into mother alloy in vacuum melting furnace;
Maintain vacuum, wherein will throw and have the described vacuum melting furnace of described mother alloy to maintain under vacuum wherein;
Master alloy melting, wherein heats mother alloy described in described vacuum melting furnace melting;
Regulate nitrogen (N) content, wherein nitrogen is injected to described vacuum melting furnace;
The alloy of stir-melting, the wherein mother alloy of stir-melting;
Form ingot casting, wherein the alloy by the melting that cast is stirred from described vacuum melting furnace forms ingot casting;
The ingot casting forming described in hot rolling; And
The stainless steel of hot rolling is carried out to water quenching, and to prevent carbide precipitation, described carbide reduces mechanical property and erosion resistance.
Applications Claiming Priority (5)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| KR1020090063487A KR101089714B1 (en) | 2009-07-13 | 2009-07-13 | C+N austenitic stainless steel with high strength and corrosion resistance having tungsten and fabrication method thereof |
| KR10-2009-0063487 | 2009-07-13 | ||
| KR1020090063486A KR101089718B1 (en) | 2009-07-13 | 2009-07-13 | C+N austenitic stainless steel with high strength and corrosion resistance having tungsten and molybdenum, and fabrication method thereof |
| KR10-2009-0063486 | 2009-07-13 | ||
| PCT/KR2009/004642 WO2011007921A1 (en) | 2009-07-13 | 2009-08-20 | High strength / corrosion-resistant,.austenitic stainless steel with carbon - nitrogen complex additive, and method for manufacturing same |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN102428200A CN102428200A (en) | 2012-04-25 |
| CN102428200B true CN102428200B (en) | 2014-04-02 |
Family
ID=43449524
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN200980159318.1A Active CN102428200B (en) | 2009-07-13 | 2009-08-20 | High strength/corrosion-resistant austenitic stainless steel with carbon - nitrogen complex additive, and method for manufacturing same |
Country Status (5)
| Country | Link |
|---|---|
| US (1) | US20110226391A1 (en) |
| EP (1) | EP2455508B1 (en) |
| JP (1) | JP5272078B2 (en) |
| CN (1) | CN102428200B (en) |
| WO (1) | WO2011007921A1 (en) |
Families Citing this family (16)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2013114825A (en) * | 2011-11-25 | 2013-06-10 | Nisshin Steel Co Ltd | Electrode laminate and lithium ion secondary battery using the same |
| KR101377251B1 (en) * | 2011-12-13 | 2014-03-26 | 한국기계연구원 | C+N austenitic stainless steel having good low-temperature toughness and a fabrication method or the same |
| EP2617839A1 (en) * | 2012-01-18 | 2013-07-24 | MeKo Laserstrahl-Materialbearbeitungen e.K. | Nickel-free iron alloy for stents |
| CN103266283A (en) * | 2013-05-17 | 2013-08-28 | 江苏星火特钢有限公司 | Non-magnetic stainless steel for ore selection equipment |
| EP2813906A1 (en) * | 2013-06-12 | 2014-12-17 | Nivarox-FAR S.A. | Part for clockwork |
| CH708231B1 (en) * | 2013-06-27 | 2017-03-15 | Nivarox Far Sa | Clock spring made of austenitic stainless steel. |
| EP2924514B1 (en) * | 2014-03-24 | 2017-09-13 | Nivarox-FAR S.A. | Clockwork spring made of austenitic stainless steel |
| CN104367362A (en) * | 2014-11-04 | 2015-02-25 | 无锡贺邦金属制品有限公司 | Alloy microscopy vascular clamp with antiallergic function |
| CN106148852A (en) * | 2015-04-02 | 2016-11-23 | 上海微创医疗器械（集团）有限公司 | A kind of alloy material and implantable medical devices |
| EP3147378A1 (en) | 2015-09-25 | 2017-03-29 | The Swatch Group Research and Development Ltd. | Nickel-free austenitic stainless steel |
| EP3249059A1 (en) * | 2016-05-27 | 2017-11-29 | The Swatch Group Research and Development Ltd. | Method for thermal treatment of austenitic steels and austenitic steels thus obtained |
| US10639719B2 (en) | 2016-09-28 | 2020-05-05 | General Electric Company | Grain boundary engineering for additive manufacturing |
| EP3327151A1 (en) * | 2016-11-04 | 2018-05-30 | Richemont International S.A. | Resonator for a clock piece |
| CN113737091A (en) * | 2021-07-22 | 2021-12-03 | 洛阳双瑞特种装备有限公司 | Steel for low-magnetism high-strength corrosion-resistant fastener and fastener |
| CN114606430B (en) * | 2022-03-01 | 2023-05-12 | 兴机电器有限公司 | Low-carbon Fe-Mn-Al-Si TWIP steel and preparation method thereof |
| CN115652210B (en) * | 2022-11-07 | 2023-05-12 | 鞍钢股份有限公司 | Austenitic stainless steel billet with ultralow carbide content and manufacturing method thereof |
Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| GB744599A (en) * | 1952-05-30 | 1956-02-08 | Armco Int Corp | Stainless steel articles for use at high temperatures |
| US3681058A (en) * | 1969-11-12 | 1972-08-01 | Crucible Inc | Low-nickel valve steel |
| CN101372721A (en) * | 2008-09-19 | 2009-02-25 | 山西太钢不锈钢股份有限公司 | High vacuum induction furnace nitrogen-containing steel smelting nitrogen pickup method |
Family Cites Families (13)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US2698785A (en) * | 1952-12-31 | 1955-01-04 | Armco Steel Corp | Age-hardening austenitic stainless steel |
| GB778597A (en) * | 1955-02-15 | 1957-07-10 | Ford Motor Co | Improvements in or relating to the manufacture of nitrogen-rich wrought austenitic alloys |
| DE2118072C3 (en) * | 1971-04-14 | 1984-05-24 | První brněnská strojírna, oborový podnik, Brno | Use of an austenitic manganese chrome steel for objects that are resistant to cavitation and erosion |
| JPH09249940A (en) * | 1996-03-13 | 1997-09-22 | Sumitomo Metal Ind Ltd | High strength steel excellent insulfide stress cracking resistance and its production |
| JP4116134B2 (en) * | 1998-02-27 | 2008-07-09 | 日本冶金工業株式会社 | Austenitic stainless steel excellent in high temperature sag resistance and method for producing the same |
| JP2000192194A (en) * | 1998-12-24 | 2000-07-11 | Hitachi Metals Ltd | Metal plate of high hardness and high expansion alloy excellent in thermal setting resistance, and its manufacture |
| EP1194605A1 (en) * | 1999-06-24 | 2002-04-10 | Basf Aktiengesellschaft | Nickel-poor austenitic steel |
| JP4178670B2 (en) * | 1999-06-28 | 2008-11-12 | セイコーエプソン株式会社 | Manganese alloy steel and shaft, screw member |
| JP4538966B2 (en) * | 2001-02-05 | 2010-09-08 | 大同特殊鋼株式会社 | High strength and high corrosion resistance nonmagnetic stainless steel |
| KR100538692B1 (en) * | 2003-12-09 | 2005-12-23 | 한국기계연구원 | High nitrogen stainless steel and method for manufacturing the hige nttrogen stainless steel utllizing low pressure induction melitng |
| KR100641577B1 (en) * | 2005-04-19 | 2006-10-31 | 주식회사 포스코 | Austenitic Stainless steel with High Mn and N |
| DE102006033973A1 (en) * | 2006-07-20 | 2008-01-24 | Technische Universität Bergakademie Freiberg | Stainless austenitic cast steel and its use |
| KR100926965B1 (en) * | 2007-10-02 | 2009-11-17 | 한국기계연구원 | High strength, high ductility stainless steel rolled sheet using transformation organic plasticity |
-
2009
- 2009-08-20 JP JP2011522918A patent/JP5272078B2/en not_active Expired - Fee Related
- 2009-08-20 WO PCT/KR2009/004642 patent/WO2011007921A1/en active Application Filing
- 2009-08-20 US US12/994,815 patent/US20110226391A1/en not_active Abandoned
- 2009-08-20 EP EP09847378.8A patent/EP2455508B1/en active Active
- 2009-08-20 CN CN200980159318.1A patent/CN102428200B/en active Active
Patent Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| GB744599A (en) * | 1952-05-30 | 1956-02-08 | Armco Int Corp | Stainless steel articles for use at high temperatures |
| US3681058A (en) * | 1969-11-12 | 1972-08-01 | Crucible Inc | Low-nickel valve steel |
| CN101372721A (en) * | 2008-09-19 | 2009-02-25 | 山西太钢不锈钢股份有限公司 | High vacuum induction furnace nitrogen-containing steel smelting nitrogen pickup method |
Also Published As
| Publication number | Publication date |
|---|---|
| US20110226391A1 (en) | 2011-09-22 |
| CN102428200A (en) | 2012-04-25 |
| EP2455508B1 (en) | 2016-11-23 |
| EP2455508A4 (en) | 2014-03-05 |
| EP2455508A1 (en) | 2012-05-23 |
| JP2011526969A (en) | 2011-10-20 |
| WO2011007921A1 (en) | 2011-01-20 |
| JP5272078B2 (en) | 2013-08-28 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN102428200B (en) | High strength/corrosion-resistant austenitic stainless steel with carbon - nitrogen complex additive, and method for manufacturing same | |
| JP4941854B2 (en) | Solidified powder metallurgy article, steel wire made from the article, and method for producing the steel wire | |
| CN103380217B (en) | The hot-rolled steel sheet product be made up of Multiphase Steel and manufacture method thereof | |
| RU72697U1 (en) | STAINLESS STEEL HIGH STRENGTH STEEL BAR | |
| JP6488287B2 (en) | Corrosion resistant wear resistant cold work tool steel | |
| JP5755153B2 (en) | High corrosion resistance austenitic steel | |
| JP2009503257A (en) | Corrosion resistance, cold formability, machinability high strength martensitic stainless steel | |
| CN111183240A (en) | Stainless steel, prealloyed powder obtained by atomizing steel and use of prealloyed powder | |
| CN101684542A (en) | Duplex stainless steel with pitting corrosion resistance and favourable cold temperature flexibility and manufacturing method thereof | |
| CN113015818B (en) | High strength non-magnetic austenitic stainless steel and method for manufacturing same | |
| CN101215671B (en) | Material capable of resisting zinc solution corrosive wear and manufacturing method thereof | |
| US20130149188A1 (en) | C+n austenitic stainless steel having good low-temperature toughness and a fabrication method thereof | |
| CN104152818A (en) | Duplex stainless steel and preparation method thereof | |
| KR101089718B1 (en) | C+N austenitic stainless steel with high strength and corrosion resistance having tungsten and molybdenum, and fabrication method thereof | |
| KR100956283B1 (en) | An austenitic stainless steel with high strength and corrosion resistance having carbon and nitrogen | |
| CN105714183A (en) | Vanadium-titanium-containing ductile cast iron material and thermal treatment process | |
| CN113913679A (en) | Cold work tool steel | |
| CN101871081B (en) | Steel for low-steel-grade continuous oil pipe and manufacturing method thereof | |
| CN105483562A (en) | High-bending-resistance, high-strength and high-toughness die steel and manufacturing method thereof | |
| CN101333625A (en) | High temperature resistant and abrasion resistant martensitic stainless steel and preparation method | |
| KR101211032B1 (en) | High-nitrogen austenitic stainless steels with good Eco-index and excellent pitting corrosion resistance, and fabrication methods thereof | |
| CN107779759B (en) | The excellent boracic bainite rail of resistance for delayed fracture and its production method | |
| WO2018056884A1 (en) | Hot work tool steel | |
| KR101089714B1 (en) | C+N austenitic stainless steel with high strength and corrosion resistance having tungsten and fabrication method thereof | |
| KR101203539B1 (en) | High nitrogen austenitic stainless steels with high mechanical properties and excellent resistance to pitting corrosion and fabrication methods thereof |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| C06 | Publication | ||
| PB01 | Publication | ||
| C10 | Entry into substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| C14 | Grant of patent or utility model | ||
| GR01 | Patent grant | ||
| TR01 | Transfer of patent right |
Effective date of registration: 20210226 Address after: Han Guoqingshangnandao Patentee after: Korea Institute of materials Address before: Han Guodatianshi Patentee before: KOREA INSTITUTE OF MACHINERY & MATERIALS |
|
| TR01 | Transfer of patent right |