CN106319396A - High-temperature-resistant seamless stainless steel tube and preparation method thereof - Google Patents
High-temperature-resistant seamless stainless steel tube and preparation method thereof Download PDFInfo
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- CN106319396A CN106319396A CN201610791480.7A CN201610791480A CN106319396A CN 106319396 A CN106319396 A CN 106319396A CN 201610791480 A CN201610791480 A CN 201610791480A CN 106319396 A CN106319396 A CN 106319396A
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/10—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of tubular bodies
- C21D8/105—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of tubular bodies of ferrous alloys
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- 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
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/005—Ferrous alloys, e.g. steel alloys containing rare earths, i.e. Sc, Y, Lanthanides
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/008—Ferrous alloys, e.g. steel alloys containing tin
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—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
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
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- 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
- C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/52—Ferrous alloys, e.g. steel alloys containing chromium with nickel with cobalt
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/001—Austenite
Abstract
The invention discloses a high-temperature-resistant seamless stainless steel tube and a preparation method thereof. The high-temperature-resistant seamless stainless steel tube comprises the following chemical components in percentage by mass: not greater than 0.02% of carbon, 0.2-0.4% of nitrogen, 1.2-1.5% of manganese, 18-20% of chromium, 9-10% of nickel, 0.4-0.6% of silicon, 1.5-2.4% of tantalum, 0.5-0.8% of vanadium, 1.6-2.4% of hafnium, 0.6-0.9% of zirconium, 2.3-3.4% of tungsten, 0.06-0.09% of yttrium, 0.03-0.05% of scandium, 0.01-0.02% of phosphorus. 0.1-0.3% of tin, 0.5-0.7% of indium, 0.3-0.5% of strontium, 0.4-0.6% of caesium, 4-7% of boron, 0.3-0.5% of cobalt, 0.4-0.7% of tellurium and the balance iron. The high-temperature-resistant seamless stainless steel tube is excellent in corrosion resistance, high in hardness and strength, excellent in high-temperature resistance, and high in ductility and toughness.
Description
Technical field
The present invention relates to a kind of austenitic stainless steel, be specifically related to a kind of high temperature resistant gapless stainless steel tube and preparation side thereof
Method.
Background technology
Prepare the gapless stainless steel tube of conveyance conduit, stainless steel material to be used, but be provided simultaneously with high-strength and high ductility performance
With the stainless steel material of excellent corrosion resistance very little, traditional ordinary carbon steel and low Cr steel steel are all difficult to meet requirement.
Martensitic stain less steel and austenite-ferrite two phase stainless steel is the most generally used to prepare high intensity seamless rustless steel
Pipe, wherein martensitic stain less steel is higher because of carbon containing, therefore has higher intensity, hardness and wearability, but its corrosion resistance is slightly worse, main
Being used for preparing the part that mechanical property requirements is higher, corrosion resisting property requirement is general, the application in conveyance conduit then limits
Bigger.
Austenite-ferrite two phase stainless steel is the rustless steel that austenite and ferritic structure respectively account for half.Containing C relatively
In the case of low, Cr content is 18%～28%, and Ni content is 3%～10%.Such steel has austenite and ferrite stainless concurrently
The feature of steel, with ferritic phase ratio, plasticity, toughness are higher, and without brittleness at room temperature, intergranular corrosion resistance performance and welding performance are the most notable
Improving, the 475 DEG C of fragility and the heat conductivity that the most also maintain ferritic stainless steel are high, have the features such as superplasticity.With Austria
Family name's body rustless steel is compared, and intensity height and intergranular corrosion resistance and resistance to chloride stress corrosion are significantly improved.
But the high-load Cr in austenite-ferrite two phase stainless steel can weaken the formation of austenite phase, makes ferritic phase
Becoming the phase constituent taken as the leading factor, this allows for putting down between austenite phase and ferritic phase in austenite-ferrite two phase stainless steel
Weighing apparatus can not get well controlling, and its performance also can be difficult to intended change, often occurs that plasticity is poor, as-welded ductility and anti-corrosion
The shortcomings such as property substantially reduction.
Ultra-low carbon austenitic stainless steel is relatively low because of carbon content ratio, and probability relatively other stainless steel-like materials of intercrystalline corrosion occur
Little, higher Cr, Ni content makes it have excellent anti-CO2、H2S and C1 corrosive nature, and the high temperature high voltage resistant of such steel
Can be good, possess the basic demand preparing conveyance conduit.But it is for needing the conveyance conduit used in harsh corrosive environment, existing
The decay resistance having ultra-low carbon austenitic stainless steel still has much room for improvement.
Summary of the invention
The goal of the invention of the present invention is to provide a kind of ultra-low carbon austenitic stainless steel, solves existing austenitic stainless steel
The problem that decay resistance is relatively low.
A kind of ultra-low carbon austenitic stainless steel, by mass percentage, its chemical analysis includes: carbon≤0.02%, nitrogen 0.2
～0.4%, manganese 1.2～1.5%, chromium 18～20%, nickel 9～10%, silicon 0.4～0.6%, tantalum 1.5～2.4%, vanadium 0.5～
0.8%, hafnium 1.6～2.4%, zirconium 0.6～0.9%, tungsten 2.3～3.4%, yttrium 0.06～0.09%, scandium 0.03～0.05%, phosphorus
0.01～0.02%, stannum 0.1～0.3%, indium 0.5～0.7%, strontium 0.3～0.5%, caesium 0.4～0.6%, boron 4～7%, cobalt
0.3～0.5%, tellurium 0.4～0.7%, surplus is ferrum.
Carbon content in austenitic stainless steel is arranged on less than 0.02% by the present invention, to prevent intercrystalline corrosion；With
The nitrogen of Shi Tianjia can be collaborative with carbon to make up the rustless steel intensity deficiency problem caused because carbon content reduces, and nitrogen is also Ovshinsky
Body forms element, plays an important role the stability of austenite structure；The addition of nitrogen can also improve the resistance to of austenitic stainless steel
Corrosive nature.
Chromium content in austenitic stainless steel is set slightly above 18% by the present invention, is improving the strong of austenitic stainless steel
While degree, hardness and wearability, it is to avoid high chrome contents affects plasticity and the toughness of austenitic stainless steel.Nickel is as strong austenite
Form element, austenitic stainless steel after mixing with rational ratio with chromium, can be made at room temperature to have stable austenite structure.
Nickel with chromium coordinated, can also improve resistance to stress corrosion resistance, high-temperature oxidation resistance and the intensity of austenitic stainless steel.
The present invention also with the addition of tantalum, vanadium, zirconium, hafnium and tungsten in austenitic stainless steel, and these alloying elements all can be excellent with carbon
First chemical combination, it is to avoid because forming Cr23C6And cause Cr depletion zone, it is effectively improved the intergranular corrosion resistance ability of austenitic stainless steel.
Wherein, tantalum has a high corrosion resistance, either under cold or heat condition, and all will not be with hydrochloric acid, concentrated nitric acid
And chloroazotic acid reacts；At 150 DEG C, tantalum also will not be corroded by concentrated sulphuric acid and inorganic salt；At normal temperatures, aqueous slkali, chlorine
Gas, bromine water, dilute sulfuric acid and other many medicaments all will not work with tantalum.The addition of tantalum can not only be effectively improved austenite not
The rust steel corrosion-resistant effect to all kinds of corrosive substances, makes austenitic stainless steel be rich in high ductibility and toughness, it is to avoid to produce crisp
Property crackle；Tantalum can also form solid solution and carbide with carbon, with the resistance to crystalline substance that vanadium coordinated improves austenitic stainless steel further
Between corrosive power；Tantalum can also form solid solution and nitride with nitrogen, improve further austenitic stainless steel decay resistance and
Intensity.
And zirconium is owing to having surprising corrosion resistance, high fusing point, the hardness of superelevation and intensity, the most only by
For Aero-Space, military project, nuclear reaction or atomic energy field, the most also it is not used for preparing the austenitic stainless steel of conveyance conduit
In.The addition of zirconium can not only improve the corrosion resistance of austenitic stainless steel, hardness, intensity and resistance to elevated temperatures, makes austenite
Rustless steel has certain plasticity, moreover it is possible to the intensity that further improves austenitic stainless steel collaborative with tantalum and resistance to elevated temperatures, also
Can be with stannum, ferrum, chromium, the collaborative intensity of austenitic stainless steel, decay resistance and the heat conductivity of improving further of nickel, reduction austenite
The stainless steel watch surface state sensitivity to corrosion.
The addition of hafnium can improve the corrosion resistance of austenitic stainless steel, hardness, intensity and resistance to elevated temperatures equally；And hafnium
Decay resistance and the intensity of austenitic stainless steel with zirconium coordinated, can be improved further.
The tungsten carbide that tungsten is formed with carbon can improve the hardness of austenitic stainless steel, wearability and heat-resisting quantity further
Energy；And cobalt is not only austenite former, moreover it is possible to the intensity that further improves austenitic stainless steel collaborative with tungsten carbide.
Being added with scandium and yttrium in the austenitic stainless steel of the present invention, both elements can not only significantly improve austenite not
The intensity of rust steel and hardness, and can be with zirconium, the collaborative resistance to elevated temperatures improving austenitic stainless steel further of hafnium；Can be with
Stannum, indium work in coordination with the enhancing compactness of austenitic stainless steel, wearability and corrosion resistance.
Being added with strontium and caesium in the austenitic stainless steel of the present invention, both elements can be worked in coordination with tantalum, makes austenite not
Rust steel has more excellent ductility and toughness.
The austenitic stainless steel of the present invention is added with carbide and nitrogen that silicon, phosphorus and tellurium, these three element and carbon are formed
The nitride formed and the boride formed with boron can be filled in the space of austenite structure, make austenite structure have
Higher compactness, is conducive to strengthening the hardness of austenitic stainless steel, intensity and resistance to elevated temperatures.
Further, silicon can also make austenitic stainless steel have certain corrosion resistance to concentrated nitric acid, and phosphorus can also make austenite
Rustless steel has certain plasticity and toughness, and tellurium can also improve the hardness of austenitic stainless steel, phosphorus and tellurium all can improve Austria
The stainless machinability of family name's body.
As preferably, by mass percentage, its chemical analysis includes: carbon≤0.02%, nitrogen 0.26～0.34%, manganese
1.36～1.42%, chromium 19.1～19.7%, nickel 9.4～9.7%, silicon 0.48～0.54%, tantalum 1.83～2.11%, vanadium 0.64
～0.73%, hafnium 1.79～2.02%, zirconium 0.75～0.83%, tungsten 2.76～3.08%, yttrium 0.07～0.09%, scandium 0.04～
0.05%, phosphorus 0.01～0.02%, stannum 0.16～0.24%, indium 0.62～0.67%, strontium 0.35～0.44%, caesium 0.47～
0.53%, boron 5～6%, cobalt 0.39～0.46%, tellurium 0.55～0.63%, surplus is ferrum.
As further preferably, by mass percentage, its chemical analysis includes: carbon 0.02%, nitrogen 0.29%, manganese
1.38%, chromium 19.5%, nickel 9.6%, silicon 0.51%, tantalum 1.98%, vanadium 0.67%, hafnium 1.94%, zirconium 0.81%, tungsten
2.95%, yttrium 0.083%, scandium 0.044%, phosphorus 0.012%, stannum 0.19%, indium 0.65%, strontium 0.41%, caesium 0.51%, boron
5.7%, cobalt 0.42%, tellurium 0.58%, surplus is ferrum.
Another goal of the invention of the present invention is to provide a kind of high temperature resistant gapless stainless steel tube, and this gapless stainless steel tube uses
Described ultra-low carbon austenitic stainless steel is prepared from.
Another goal of the invention of the present invention is to provide the preparation method of a kind of described high temperature resistant gapless stainless steel tube, this system
Preparation Method comprises the following steps:
S1: each raw material of described ultra-low carbon austenitic stainless steel is placed in electric furnace or converter after carrying out just refining and carries out essence
Refining, by acquisition refining liquid continuous casting or be molded into steel billet；
S2: under argon atmosphere, selects ingot shape that described steel billet is carried out electroslag remelting, quickly cools down acquisition after remelting
Ingot casting；
S3: described ingot casting is carried out homogenizing anneal；
S4: the ingot casting after homogenizing anneal is heated to 1100-1250 DEG C, is incubated more than 30min, carries out many to ingot casting
Passage is forged, and makes forging stock；
S5: strip off the skin centering and perforation process to described forging stock, makes pipe；
S6: described pipe is carried out hot extrusion, makes seamless tube blank；
S7: described seamless tube blank is carried out solution treatment；
S8: the seamless tube blank after solution treatment is carried out cold deformation process, makes the contraction percentage of area control 20～40%
Between, it is thus achieved that gapless stainless steel tube semi-finished product；
S9: described seamless pipe semi-finished product are carried out stress relief annealing, the most qualified after obtain described high temperature resistant seamless not
Rust steel pipe finished product.
As preferably, in step S1, described just refining includes:
S1-1: by the mass percent preset, manganese, nickel, chromium, yttrium, scandium, indium, strontium, caesium and ferrum are placed in electric furnace or converter
In, at 1350-1450 DEG C, carry out melting, the most melted to all the components, it is thus achieved that melting liquid A；
S1-2: by the mass percent preset, tantalum, hafnium, zirconium, tungsten, vanadium, stannum, phosphorus, tellurium and cobalt are placed in electric furnace or converter
In, at 1480～1650 DEG C, carry out melting, the most melted to all the components, it is thus achieved that melting liquid B；
S1-3: melting liquid B is warming up to 1580-1720 DEG C, and by the mass percent preset, add in melting liquid B
Carbon, nitrogen, boron and silicon, continue melting 3～4h, it is thus achieved that melting liquid C；
S1-4: joined by melting liquid A in the melting liquid C of 1580-1720 DEG C, be heated to 1680～1820 DEG C, is incubated 30
～60min, it is thus achieved that just refine liquid.
The present invention individually by the melting together with cobalt of tantalum, hafnium, zirconium, tungsten, vanadium, stannum, phosphorus, tellurium, and by preferential for melting liquid B with
The melting together with silicon of carbon, nitrogen, boron, at a proper temperature, makes carbon, boron, the nitrogen alloying element preferentially and in melting liquid B and silicon shape
Become solid solution, carbide, nitride and boride, melting liquid C and melting liquid A is mixed acquisition the most again and just refines liquid, it is to avoid because of
Carbon forms carbide with chromium and intercrystalline corrosion occurs.
As preferably, in step S1, described refine includes: be placed in AOD furnace, described just refining liquid in 1860～1950 DEG C
Under carry out refine, be incubated 3～3.5h, it is thus achieved that described refining liquid.
As preferably, in step S3, described homogenizing anneal includes with the next stage:
First stage: described ingot casting is heated to 1150～1230 DEG C, it is incubated 10～12h；
Second stage: from 1150～1230 DEG C, annealing temperature is warming up to 1320～1350 DEG C, is incubated 8～11h；
Phase III: annealing temperature is down to 1260～1280 DEG C from 1320～1350 DEG C, it is incubated 10～13h；
Fourth stage: from 1260～1280 DEG C, annealing temperature is down to 1150～1230 DEG C, is incubated 4～6h.
Homogenizing anneal is divided into four-stage by the present invention, is gradually lowered after annealing temperature being gradually risen, can not only
Effectively eliminate component segregation, moreover it is possible to avoid firm Quality Down and high energy consumption problem that long heating environment caused；Make
While all kinds of solid solution and carbide incorporate in austenite structure, it is to avoid stay at solid solution and carbide shared position originally
Lower cavity, forms micro-flaw.
As preferably, in step S6, described hot extrusion comprises the following steps:
S6-1: described pipe is placed in annular furnace preheating, and annular furnace temperature is set to 1080～1120 DEG C, the time in stove
For 1.4d min, wherein d is the wall thickness of described pipe；
S6-2: being placed in induction furnace by the pipe after preheating and once heat, induction furnace temperature is 1160～1180 DEG C,
Insulation 3～5min；
S6-3: once after heating, utilize glass dust that the surfaces externally and internally of pipe is lubricated；
S6-4: after lubrication, carries out expanding process to pipe；
S6-5: after expanding, is placed in pipe in induction furnace and carries out post bake, and induction furnace temperature is 1240～1270 DEG C,
Insulation 3～6min；
S6-6: after post bake, is squeezed into seamless tube blank, air cooling by pipe.
As preferably, in step S7, described solution treatment is: described seamless tube blank is heated to 1050～1150 DEG C, protects
Water-cooled after temperature 10～30min.
Compared with prior art, the invention have the benefit that
(1) carbon content in austenitic stainless steel is arranged on less than 0.02% by the present invention, to prevent intercrystalline corrosion；
The nitrogen simultaneously added can be collaborative with carbon to make up the rustless steel intensity deficiency problem caused because carbon content reduces, and nitrogen is also difficult to understand
Family name's body forms element, plays an important role the stability of austenite structure；The addition of nitrogen can also improve austenitic stainless steel
Decay resistance；
(2) the chromium content in austenitic stainless steel is set slightly above 18% by the present invention, is improving austenitic stainless steel
Intensity, hardness and wearability while, it is to avoid high chrome contents affects plasticity and the toughness of austenitic stainless steel；Nickel is as strong difficult to understand
Family name's body forms element, and austenitic stainless steel can be made after mixing with rational ratio with chromium at room temperature to have stable austenite group
Knit；Nickel with chromium coordinated, can also improve resistance to stress corrosion resistance, high-temperature oxidation resistance and the intensity of austenitic stainless steel；
(3) present invention with the addition of tantalum, vanadium, zirconium, hafnium and tungsten in austenitic stainless steel, and these alloying elements all can be excellent with carbon
First chemical combination, it is to avoid because forming Cr23C6And cause Cr depletion zone, it is effectively improved the intergranular corrosion resistance ability of austenitic stainless steel；
Wherein, the addition of tantalum can not only be effectively improved the austenitic stainless steel corrosion-resistant effect to all kinds of corrosive substances,
Austenitic stainless steel is made to be rich in high ductibility and toughness, it is to avoid to produce brittle crack；Tantalum can also form solid solution and carbonization with carbon
Thing, with the intergranular corrosion resistance ability that vanadium coordinated improves austenitic stainless steel further；Tantalum can also with nitrogen formed solid solution and
Nitride, improves decay resistance and the intensity of austenitic stainless steel further；
The addition of zirconium can not only improve the corrosion resistance of austenitic stainless steel, hardness, intensity and resistance to elevated temperatures, makes Austria
Family name's body rustless steel has certain plasticity, moreover it is possible to the intensity that further improves austenitic stainless steel collaborative with tantalum and heat-resisting quantity
Can, moreover it is possible to stannum, ferrum, chromium, the nickel collaborative raising further intensity of austenitic stainless steel, decay resistance and heat conductivity, reduce
The austenitic stainless steel apparent condition sensitivity to corrosion；
The addition of hafnium can improve the corrosion resistance of austenitic stainless steel, hardness, intensity and resistance to elevated temperatures equally；And hafnium
Decay resistance and the intensity of austenitic stainless steel with zirconium coordinated, can be improved further；
The tungsten carbide that tungsten is formed with carbon can improve the hardness of austenitic stainless steel, wearability and heat-resisting quantity further
Energy；And cobalt and nickel are not only austenite former, moreover it is possible to the intensity that further improves austenitic stainless steel collaborative with tungsten carbide；
(4) being added with scandium and yttrium in the austenitic stainless steel of the present invention, both elements can not only significantly improve Ovshinsky
The stainless intensity of body and hardness, and can be with zirconium, the collaborative resistance to elevated temperatures improving austenitic stainless steel further of hafnium；Energy
Enough and stannum, indium work in coordination with the enhancing compactness of austenitic stainless steel, wearability and corrosion resistance；
(5) being added with strontium and caesium in the austenitic stainless steel of the present invention, both elements can be worked in coordination with tantalum, makes austenite
Rustless steel has more excellent ductility and toughness；
(6) austenitic stainless steel of the present invention is added with silicon, phosphorus and tellurium, carbide that these three element and carbon are formed,
The nitride formed with nitrogen and the boride formed with boron can be filled in the space of austenite structure, make austenite structure
There is higher compactness, be conducive to strengthening the hardness of austenitic stainless steel, intensity and resistance to elevated temperatures；
Further, silicon can also make austenitic stainless steel have certain corrosion resistance to concentrated nitric acid, and phosphorus can also make austenite
Rustless steel has certain plasticity and toughness, and tellurium can also improve the hardness of austenitic stainless steel, phosphorus and tellurium all can improve Austria
The stainless machinability of family name's body.
Detailed description of the invention
Detailed description of the invention is set forth below technical scheme is described in further detail.
Embodiment 1
The present embodiment one ultra-low carbon austenitic stainless steel, by mass percentage, its chemical analysis includes: carbon
0.02%, nitrogen 0.29%, manganese 1.38%, chromium 19.5%, nickel 9.6%, silicon 0.51%, tantalum 1.98%, vanadium 0.67%, hafnium
1.94%, zirconium 0.81%, tungsten 2.95%, yttrium 0.083%, scandium 0.044%, phosphorus 0.012%, stannum 0.19%, indium 0.65%, strontium
0.41%, caesium 0.51%, boron 5.7%, cobalt 0.42%, tellurium 0.58%, surplus is ferrum.
Embodiment 2～5
By mass percentage, the chemical analysis of the ultra-low carbon austenitic stainless steel of embodiment 2～5 is as shown in table 1.
The chemical analysis table of the ultra-low carbon austenitic stainless steel of table 1 embodiment 2～5
Comparative example 1～17
By mass percentage, in comparative example 1～19 chemical analysis of austenitic stainless steel as shown in table 2, table 3 and table 4.
The chemical analysis table of austenitic stainless steel in table 2 comparative example 1～9
The chemical analysis table of austenitic stainless steel in table 3 comparative example 10～17
The chemical analysis table of austenitic stainless steel in table 4 comparative example 18～25
Embodiment 6
Be utilized respectively embodiment 1～5 and the austenitic stainless steel material of comparative example 1～25 prepare high temperature resistant seamless stainless steel
Pipe, comprises the following steps:
(1) just refine
1.: by the mass percent preset, manganese, nickel, chromium, yttrium, scandium, indium, strontium, caesium and ferrum are placed in electric furnace or converter,
Melting is carried out at 1350-1450 DEG C, the most melted to all the components, it is thus achieved that melting liquid A；
2.: by the mass percent preset, tantalum, hafnium, zirconium, tungsten, vanadium, stannum, phosphorus, tellurium and cobalt are placed in electric furnace or converter,
Melting is carried out at 1480～1650 DEG C, the most melted to all the components, it is thus achieved that melting liquid B；
3.: melting liquid B is warming up to 1580-1720 DEG C, and by preset mass percent, in melting liquid B add carbon,
Nitrogen, boron and silicon, continue melting 3～4h, it is thus achieved that melting liquid C；
4.: melting liquid A is joined in the melting liquid C of 1580-1720 DEG C, be heated to 1680～1820 DEG C, insulation 30～
60min, it is thus achieved that just refine liquid.
(2) refine
It is placed in just refining liquid in AOD furnace, at 1860～1950 DEG C, carries out refine, be incubated 3～3.5h, it is thus achieved that refining liquid,
Acquisition refining liquid is molded intoSteel billet.
(3) electroslag remelting
With argon shield electroslag refining furnace, steel billet is carried out electroslag remelting, after remelting, quickly cool down acquisition's
Ingot casting.
(4) homogenizing anneal
First stage: ingot casting is heated to 1150～1230 DEG C, it is incubated 10～12h；
Second stage: from 1150～1230 DEG C, annealing temperature is warming up to 1320～1350 DEG C, is incubated 8～11h；
Phase III: annealing temperature is down to 1260～1280 DEG C from 1320～1350 DEG C, it is incubated 10～13h；
Fourth stage: from 1260～1280 DEG C, annealing temperature is down to 1150～1230 DEG C, is incubated 4～6h.
(5) forging
Ingot casting after homogenizing anneal is heated to 1100-1250 DEG C, is incubated 60min, ingot casting is carried out multi-pass forging
Make, make forging stock.
(6) tubulation base
Strip off the skin centering and perforation process to forging stock, makesPipe.
(7) hot extrusion
1.: pipe is placed in annular furnace preheating, annular furnace temperature is set to 1080～1120 DEG C, and the time in stove is
700min (i.e. 1.4 × 500)；
2.: being placed in induction furnace by the pipe after preheating and once heat, induction furnace temperature is 1160～1180 DEG C, protects
Temperature 3～5min；
3.: once after heating, utilize 1100～1250 DEG C of molten glass powder that the surfaces externally and internally of pipe is lubricated；
4.: after lubrication, use rose bit that pipe is carried out expanding process；
5.: after expanding, being placed in induction furnace by pipe and carry out post bake, induction furnace temperature is 1240～1270 DEG C, protects
Temperature 3～6min；
6.: after post bake, pipe is squeezed into seamless tube blank, air cooling, it is thus achieved that seamless tube blank external diameter be 327mm, wall
Thick 21.4mm.
(8) solution treatment
Seamless tube blank is heated to 1050～1150 DEG C, after insulation 20min, water-cooled, aligning, pickling, reconditioning, lubrication.
(9) cold deformation processes
Seamless tube blank after solution treatment is carried out cold deformation process, make the contraction percentage of area control 20～40% it
Between, it is thus achieved that gapless stainless steel tube semi-finished product；
(10) stress relief annealing
At 600～800 DEG C, gapless stainless steel tube semi-finished product are carried out stress relief annealing, it is thus achieved that high temperature resistant seamless stainless steel
Pipe finished product.
(11) Non-Destructive Testing
By ASME E213 " metal nominal pipe and the practical code of pipe ultrasonic inspection " to obtain high temperature resistant seamless not
Rust steel pipe finished product carries out ultrasonic examination, and II grade qualified.
(12) tube end maching
Gapless stainless steel tube finished product qualified for Non-Destructive Testing is cut into the length of needs.
Test case
1, measuring mechanical property
(1) wearability test
Embodiment 1～5 and the gapless stainless steel tube for preparing of the austenitic stainless steel material of comparative example 1～13 will be used
Carrying out wearability experiment on MLD-10 type impact abrasive wear testing machine respectively, detailed process is as follows: by gapless stainless steel tube
Cutting into the sample of 10mm × 10mm × 30mm, abrasive material is the purity quartzite of 1mm～2mm, and flow is 450mL/min, impact
Merit is 5.0J；Quality after 30min measures once abrasion, measures 5 times altogether, and wear and tear 2h, judges wear-resisting with sample weightlessness
Property；Test result is shown in Table 5.
(2) hardness, impact flexibility, elongation percentage, tensile strength and yield strength test
Test result is shown in Table 5 and table 6.
The measuring mechanical property result (under room temperature) of each gapless stainless steel tube of table 5
From table 5, the gapless stainless steel tube using the ultra-low carbon austenitic stainless steel of embodiment 1～5 to prepare is respectively provided with
Excellent wearability, hardness, impact flexibility, elongation percentage, tensile strength and yield strength.
Compared with Example 1, after silicon lacks in comparative example 1, in comparative example 22 after phosphorus disappearance, comparative example 24 lacks tellurium
After, though the wearability of gapless stainless steel tube, hardness, impact flexibility, elongation percentage, tensile strength and yield strength have declined, but
Fall is less；But after in comparative example 2, silicon and boron lack simultaneously, after in comparative example 22, phosphorus and boron lack simultaneously, comparative example
After in 24, tellurium and boron lack simultaneously, the fall of every mechanical performance of gapless stainless steel tube is greatly improved.This is because boron
After disappearance, the boride that silicon, phosphorus and tellurium and boron are formed reduces, and the space of austenite structure increases, and causes gapless stainless steel tube
Every mechanical performance weakens.
Compared with Example 1, comparative example 3 is owing to disappearance tantalum, comparative example 4 are due to disappearance vanadium, gapless stainless steel tube wear-resisting
Property, hardness, impact flexibility, elongation percentage, tensile strength and yield strength are all greatly reduced；And comparative example 5 is owing to lacking tantalum simultaneously
And vanadium, comparative example 21 is due to disappearance strontium, caesium and tantalum, the wearability of gapless stainless steel tube, hardness, impact flexibility, elongation percentage, tension
Intensity and yield strength reduce further；Wherein, the declining by a big margin of impact flexibility, elongation percentage and yield strength.Show tantalum
All can be effectively improved the hardness of ultra-low carbon austenitic stainless steel of the present invention, intensity and wearability with vanadium, and make the present invention ultralow
Carbon austenitic stainless steel is rich in high ductibility and toughness, and both use or better with when strontium and caesium simultaneously.
Compared with Example 1, comparative example 6 is due to disappearance hafnium, and comparative example 7 is due to disappearance zirconium, gapless stainless steel tube wear-resisting
Property, hardness, impact flexibility, elongation percentage, tensile strength and yield strength are all greatly reduced；Comparative example 8 due to lack simultaneously hafnium and
Tantalum, comparative example 8 are owing to lacking hafnium and tantalum, comparative example 10 owing to lacking hafnium and vanadium, comparative example 11 owing to lacking simultaneously simultaneously simultaneously
Tantalum and zirconium and stannum, the wearability of gapless stainless steel tube, hardness, impact flexibility, elongation percentage, tensile strength and yield strength are further
Reduce；Wherein the declining by a big margin of wearability, hardness and tensile strength；Show that hafnium and zirconium all can be effectively improved the present invention and surpass
The hardness of low-carbon austenitic, intensity and wearability, when both use simultaneously or are combined with stannum, tantalum or vanadium, effect is more
Good.
Compared with Example 1, comparative example 12 due to disappearance tungsten, the wearability of gapless stainless steel tube, hardness, impact flexibility,
Elongation percentage, tensile strength and yield strength all decrease；Comparative example 13 owing to lacking tungsten and cobalt simultaneously, gapless stainless steel tube
Wearability, hardness, impact flexibility, elongation percentage, tensile strength and yield strength reduce further, wherein wearability, hardness and anti-
Declining by a big margin of tensile strength.This is because tungsten can form tungsten carbide with carbon, tungsten carbide can improve austenite not further
The rust hardness of steel, wearability and resistance to elevated temperatures；And cobalt is not only austenite former, moreover it is possible to collaborative with tungsten carbide further
Improve the intensity of austenitic stainless steel.
Compared with Example 1, comparative example 14 owing to lacking tantalum and tungsten simultaneously, comparative example 15 due to lack simultaneously tantalum, hafnium and
Tungsten, comparative example 16 is owing to lacking vanadium, zirconium and tungsten simultaneously, and comparative example 17 is owing to lacking tantalum, zirconium, hafnium and vanadium, seamless stainless steel simultaneously
The wearability of pipe, hardness, impact flexibility, elongation percentage, tensile strength and yield strength reduce further.Show this five kinds of alloy units
Synergism is all there is, it is possible to be effectively improved the hardness of ultra-low carbon austenitic stainless steel of the present invention, intensity and wearability between element,
And make ultra-low carbon austenitic stainless steel of the present invention be rich in high ductibility and toughness.
Compared with Example 1, comparative example 18 is due to disappearance yttrium and scandium, and the wearability of gapless stainless steel tube, hardness, impact are tough
Property, elongation percentage, tensile strength and yield strength all decrease；Comparative example 19 due to disappearance yttrium, scandium, zirconium, hafnium, comparative example 20 by
In disappearance yttrium, scandium, stannum, indium, the fall of the every mechanical performance of gapless stainless steel tube is greatly improved.This shows that yttrium and scandium can
Significantly improve intensity and the hardness of austenitic stainless steel, and can work in coordination with zirconium, hafnium and improve austenitic stainless steel further
Intensity and hardness；Compactness and the wearability strengthening austenitic stainless steel can be worked in coordination with stannum, indium.
The measuring mechanical property result (at 600 DEG C/800 DEG C) of each gapless stainless steel tube of table 6
From table 6, raising with temperature, the impact flexibility of each gapless stainless steel tube, elongation percentage, tensile strength and surrender are strong
Degree has declined, but when hafnium disappearance (comparative example 6), zirconium disappearance (comparative example 7), tungsten disappearance (comparative example 12), seamless stainless steel
Declining by a big margin of the impact flexibility of pipe, elongation percentage, tensile strength and yield strength, and hafnium and zirconium lack simultaneously (contrast
Example 8), hafnium, zirconium and stannum lack (comparative example 9) simultaneously, and vanadium and hafnium lack (comparative example 10) simultaneously, and tantalum and zirconium lack (contrast simultaneously
Example 11), tungsten and cobalt lack (comparative example 13) simultaneously, and tantalum and tungsten lack (comparative example 14) simultaneously, and it is (right that tantalum, hafnium and tungsten lack simultaneously
Ratio 15), vanadium, zirconium and tungsten lack (comparative example 16) simultaneously, when tantalum, zirconium, hafnium and vanadium lack (comparative example 17) simultaneously, seamless stainless
The fall of the impact flexibility of steel pipe, elongation percentage, tensile strength and yield strength is bigger, shows that hafnium, zirconium and tungsten are all conducive to
Improve the resistance to elevated temperatures of gapless stainless steel tube, and be combined between the addition of vanadium, tantalum and cobalt, and each alloying element and all can enter one
Step improves the resistance to elevated temperatures of gapless stainless steel tube.
2, chemical property test
By use embodiment 1～5 and the gapless stainless steel tube prepared of the austenitic stainless steel material of comparative example 1～13 respectively
It is placed in following corrosive solution:
A, mass fraction are the salpeter solution of 35%；
B, mass fraction are the hydrochloric acid solution of 26%；
C, mass fraction are the sulfuric acid solution of 65%；
D, mass fraction are the bromine water of 2.7%；
E, mass fraction are the formic acid of 5%；
At room temperature and 100 DEG C, corrode 72h respectively, detect each corrosive solution corrosion journey to each gapless stainless steel tube
Degree, testing result is shown in Table 7.
The decay resistance test result of each gapless stainless steel tube of table 7
From table 7, use gapless stainless steel tube prepared by the ultra-low carbon austenitic stainless steel of embodiment 1～5, to each corruption
Erosion solution is respectively provided with excellent decay resistance.
Comparative example 1 is due to disappearance silicon so that the corrosion resistance of each etchant solution has been weakened by gapless stainless steel tube, its
In relatively large to the corrosion resistance fall of 35% nitric acid.
When tantalum lacks (comparative example 3), vanadium disappearance (comparative example 4), hafnium disappearance (comparative example 6), during zirconium disappearance (comparative example 7),
The corrosion resistance of each etchant solution is all greatly reduced by gapless stainless steel tube；When hafnium and zirconium lack (comparative example 8) simultaneously, hafnium,
Zirconium and stannum lack (comparative example 9) simultaneously, and vanadium and hafnium lack (comparative example 10) simultaneously, and tantalum and zirconium lack (comparative example 11) simultaneously, tantalum,
When zirconium, hafnium and vanadium lack (comparative example 17) simultaneously, the corrosion resistance of each etchant solution is reduced by gapless stainless steel tube further.
This shows that tantalum, hafnium, zirconium and vanadium are all conducive to improving the decay resistance of gapless stainless steel tube, and between each alloying element, combination is equal
The decay resistance of gapless stainless steel tube can be improved further.
When tungsten disappearance (comparative example 11), although the corrosion resistance fall that gapless stainless steel tube is to each etchant solution
Less, but when tungsten lacks with cobalt, tantalum, hafnium, zirconium or vanadium simultaneously, gapless stainless steel tube is equal to the corrosion resistance of each etchant solution
Be greatly reduced, show tungsten may and cobalt, tantalum, hafnium, zirconium or vanadium between there is synergistic function, it is possible to improve further seamless not
The decay resistance of rust steel pipe.
Similarly, when yttrium and scandium lack (comparative example 18), the gapless stainless steel tube corrosion resistance to each etchant solution
Although fall is less, but when yttrium and scandium lack (comparative example 19) with zirconium and hafnium simultaneously, gapless stainless steel tube is to each corrosion
The corrosion resistance of solution is all greatly reduced, when yttrium and scandium lack (comparative example 20) with stannum and indium simultaneously, and gapless stainless steel tube
The corrosion resistance of each etchant solution is also decreased, shows between yttrium and scandium and zirconium and hafnium, between yttrium and scandium and stannum and indium
There is synergistic function, it is also possible to improve the decay resistance of gapless stainless steel tube further.
When silicon lacks (comparative example 1), phosphorus disappearance (comparative example 22), tellurium disappearance (comparative example 24), gapless stainless steel tube pair
Although the corrosion resistance fall of each etchant solution is less,
But tellurium after silicon and boron lack simultaneously in comparative example 2, after phosphorus and boron lack simultaneously in comparative example 22, in comparative example 24
After lacking with boron, the fall of every mechanical performance of gapless stainless steel tube is all greatly improved simultaneously.This is because boron disappearance
After, the boride that silicon, phosphorus and tellurium and boron are formed reduces, and the space of austenite structure increases, and causes the corrosion resistant of gapless stainless steel tube
Erosion reduced capability.
Claims (10)
1. a ultra-low carbon austenitic stainless steel, it is characterised in that by mass percentage, its chemical analysis includes: carbon≤
0.02%, nitrogen 0.2～0.4%, manganese 1.2～1.5%, chromium 18～20%, nickel 9～10%, silicon 0.4～0.6%, tantalum 1.5～
2.4%, vanadium 0.5～0.8%, hafnium 1.6～2.4%, zirconium 0.6～0.9%, tungsten 2.3～3.4%, yttrium 0.06～0.09%, scandium
0.03～0.05%, phosphorus 0.01～0.02%, stannum 0.1～0.3%, indium 0.5～0.7%, strontium 0.3～0.5%, caesium 0.4～
0.6%, boron 4～7%, cobalt 0.3～0.5%, tellurium 0.4～0.7%, surplus is ferrum.
2. ultra-low carbon austenitic stainless steel as claimed in claim 1, it is characterised in that by mass percentage, its chemistry becomes
Part includes: carbon≤0.02%, nitrogen 0.26～0.34%, manganese 1.36～1.42%, chromium 19.1～19.7%, nickel 9.4～9.7%,
Silicon 0.48～0.54%, tantalum 1.83～2.11%, vanadium 0.64～0.73%, hafnium 1.79～2.02%, zirconium 0.75～0.83%, tungsten
2.76～3.08%, yttrium 0.07～0.09%, scandium 0.04～0.05%, phosphorus 0.01～0.02%, stannum 0.16～0.24%, indium
0.62～0.67%, strontium 0.35～0.44%, caesium 0.47～0.53%, boron 5～6%, cobalt 0.39～0.46%, tellurium 0.55～
0.63%, surplus is ferrum.
3. ultra-low carbon austenitic stainless steel as claimed in claim 1, it is characterised in that by mass percentage, its chemistry becomes
Part includes: carbon 0.02%, nitrogen 0.29%, manganese 1.38%, chromium 19.5%, nickel 9.6%, silicon 0.51%, tantalum 1.98%, vanadium
0.67%, hafnium 1.94%, zirconium 0.81%, tungsten 2.95%, yttrium 0.083%, scandium 0.044%, phosphorus 0.012%, stannum 0.19%, indium
0.65%, strontium 0.41%, caesium 0.51%, boron 5.7%, cobalt 0.42%, tellurium 0.58%, surplus is ferrum.
4. a high temperature resistant gapless stainless steel tube, it is characterised in that use the Ultra-low carbon as described in claims 1 to 3 is arbitrary difficult to understand
Family name's body rustless steel is prepared from.
The preparation method of high temperature resistant gapless stainless steel tube the most as claimed in claim 4, it is characterised in that comprise the following steps:
S1: each raw material of arbitrary for claims 1 to 3 described ultra-low carbon austenitic stainless steel is placed in electric furnace or converter and carries out
Just carry out refine after refining, by acquisition refining liquid continuous casting or be molded into steel billet；
S2: under argon atmosphere, selects ingot shape that described steel billet is carried out electroslag remelting, and after remelting, quickly cooling obtains casting
Ingot；
S3: described ingot casting is carried out homogenizing anneal；
S4: the ingot casting after homogenizing anneal is heated to 1100-1250 DEG C, is incubated more than 30min, ingot casting is carried out multi-pass
Forging, makes forging stock；
S5: strip off the skin centering and perforation process to described forging stock, makes pipe；
S6: described pipe is carried out hot extrusion, makes seamless tube blank；
S7: described seamless tube blank is carried out solution treatment；
S8: the seamless tube blank after solution treatment is carried out cold deformation process, makes the contraction percentage of area control between 20～40%,
Obtain gapless stainless steel tube semi-finished product；
S9: described seamless pipe semi-finished product are carried out stress relief annealing, the described high temperature resistant seamless stainless steel of the most qualified rear acquisition
Pipe finished product.
6. preparation method as claimed in claim 5, it is characterised in that in step S1, described just refining includes:
S1-1: by the mass percent preset, manganese, nickel, chromium, yttrium, scandium, indium, strontium, caesium and ferrum are placed in electric furnace or converter,
Melting is carried out at 1350-1450 DEG C, the most melted to all the components, it is thus achieved that melting liquid A；
S1-2: by the mass percent preset, tantalum, hafnium, zirconium, tungsten, vanadium, stannum, phosphorus, tellurium and cobalt are placed in electric furnace or converter,
Melting is carried out at 1480～1650 DEG C, the most melted to all the components, it is thus achieved that melting liquid B；
S1-3: melting liquid B is warming up to 1580-1720 DEG C, and by preset mass percent, in melting liquid B add carbon,
Nitrogen, boron and silicon, continue melting 3～4h, it is thus achieved that melting liquid C；
S1-4: melting liquid A is joined in the melting liquid C of 1580-1720 DEG C, be heated to 1680～1820 DEG C, insulation 30～
60min, it is thus achieved that just refine liquid.
7. preparation method as claimed in claim 5, it is characterised in that in step S1, described refine includes: just refine liquid by described
It is placed in AOD furnace, at 1860～1950 DEG C, carries out refine, be incubated 3～3.5h, it is thus achieved that described refining liquid.
8. preparation method as claimed in claim 5, it is characterised in that in step S3, described homogenizing anneal includes following rank
Section:
First stage: described ingot casting is heated to 1150～1230 DEG C, it is incubated 10～12h；
Second stage: from 1150～1230 DEG C, annealing temperature is warming up to 1320～1350 DEG C, is incubated 8～11h；
Phase III: annealing temperature is down to 1260～1280 DEG C from 1320～1350 DEG C, it is incubated 10～13h；
Fourth stage: from 1260～1280 DEG C, annealing temperature is down to 1150～1230 DEG C, is incubated 4～6h.
9. preparation method as claimed in claim 5, it is characterised in that in step S6, described hot extrusion comprises the following steps:
S6-1: described pipe is placed in annular furnace preheating, and annular furnace temperature is set to 1080～1120 DEG C, the time in stove is
1.4d min, wherein d is the wall thickness of described pipe；
S6-2: being placed in induction furnace by the pipe after preheating and once heat, induction furnace temperature is 1160～1180 DEG C, insulation
3～5min；
S6-3: once after heating, utilize glass dust that the surfaces externally and internally of pipe is lubricated；
S6-4: after lubrication, carries out expanding process to pipe；
S6-5: after expanding, is placed in pipe in induction furnace and carries out post bake, and induction furnace temperature is 1240～1270 DEG C, is incubated 3
～6min；
S6-6: after post bake, is squeezed into seamless tube blank, air cooling by pipe.
10. preparation method as claimed in claim 5, it is characterised in that in step S7, described solution treatment is: by described nothing
Slit-tube base is heated to 1050～1150 DEG C, water-cooled after insulation 10～30min.
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Application publication date: 20170111 |