CN109439961A - A kind of high temperature alloy silk material and preparation method thereof - Google Patents
A kind of high temperature alloy silk material and preparation method thereof Download PDFInfo
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- CN109439961A CN109439961A CN201810593915.6A CN201810593915A CN109439961A CN 109439961 A CN109439961 A CN 109439961A CN 201810593915 A CN201810593915 A CN 201810593915A CN 109439961 A CN109439961 A CN 109439961A
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C19/00—Alloys based on nickel or cobalt
- C22C19/03—Alloys based on nickel or cobalt based on nickel
- C22C19/05—Alloys based on nickel or cobalt based on nickel with chromium
- C22C19/058—Alloys based on nickel or cobalt based on nickel with chromium without Mo and W
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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
- C21D8/06—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/10—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of nickel or cobalt or alloys based thereon
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Abstract
A kind of high temperature alloy silk material and preparation method thereof, by mass percentage, chemical component are as follows: Cr 15 ~ 16, Fe 7.5 ~ 8.5, Ti2.5 ~ 2.6, Nb 0.8 ~ 1.0, Al 0.6 ~ 0.9, C £ 0.06, Zr 0.05 ~ 0.08, P £ 0.008, S £ 0.008, surplus Ni;The technique controls the total deformation of each silk material and the deflection per pass of silk material using the method for annealing, pickling and cold drawing, reduces inhomogeneous deformation, obtains equally distributed tissue;As silk material size < 3mm, in addition to the deflection of control silk material, it is also necessary to which the surface quality for guaranteeing silk material using vacuum heat treatment avoids the occurrence of corrosion and other defect;The even tissue of silk material product of the invention is distributed, no layering or open grain structure;The features such as the defects of silk material surface flawless, pockmark has dimensional accuracy high, and surface quality is excellent.
Description
Technical field
The present invention relates to alloy fields more particularly to a kind of GH4145 high temperature alloy silk material and preparation method thereof.
Background technique
GH4145 alloy is mainly the nickel base superalloy that ageing strengthening is carried out with g ¢ phase, is had at 980 °C or less good
Corrosion-resistant and antioxygenic property, 800 °C or less intensity with higher, 540 °C or less have preferable resistance to relaxation property, together
When also there is good processability and welding performance.The alloy have excellent comprehensive mechanical property, can be processed into plate,
The materials such as stick, silk and band.In 800 DEG C or less work, simultaneously desired strength is higher resistance to mainly for the manufacture of aero-engine for the alloy
Loose plane spring, helical spring structure part and bolt etc., it may also be used for the parts such as manufacture gas-turbine turbo blade.For bullet
The parts such as spring need to prepare the silk material of various sizes, the especially preparation of diameter < 1mm high temperature alloy silk material, ask there are following
Topic:
(1) containing intensified elements such as a large amount of Al, Ti and Nb in GH4145 alloy, alloy molding difficulty is larger, hot processing temperature
Narrow range, cold working plasticity is low, and resistance of deformation increases, and hot processing window is relatively narrow, therefore cold and hot working difficulty is larger;
(2) complex forming technology of silk material, structural homogenity are difficult to control;
(3) silk material surface quality is poor, and due to using acid cleaning process, product surface has the defects of borrosion hole, crackle or incised wound, influences
The quality of product.
There are many factor for influencing the forming of GH4145 alloy wire, and the main degree of purity including material, is set heat processing technique
Standby, mold and cold machining process etc. couple between above-mentioned multi-parameter, and process choice is sufficiently complex;Although GH4145 alloy wire
Produced before material, but product there are nonuniform organization, frequent fracture of wire and surface quality are poor the disadvantages of, lead to silk material quality not
It is qualified, it is impossible to be used in production spring part etc.;Therefore, it is necessary to understand in depth material purity, heat processing technique, hot rolling technology,
Wire drawing process and silk material preparation process, the main selection including device parameter, the selection of mold materials, the deformation of different passages
The selection of amount, rate of deformation and annealing schedule and cooling velocity in annealing process.For example, the deflection of passage and annealing temperature
Degree control could obtain perfect recrystallization tissue in reasonable range;In addition, aviation or space flight part are to silk material dimensional accuracy
It is very high with surface quality requirements, even if the structure property of silk material is qualified, if there is shrinkage cavity trace on surface, bubble, cavity, splits
The defects of line, layering and field trash, it is off quality still to will lead to silk material.
Summary of the invention
It is an object of the present invention to provide a kind of high temperature alloy silk material and preparation method thereof, the technique is using annealing, pickling and cold
The method of drawing controls the total deformation of each silk material and the deflection per pass of silk material, reduces inhomogeneous deformation, obtains uniform
The tissue of distribution;Solves the above technical problem.
In order to achieve the above technical purposes, reach above-mentioned technical requirements, the technical scheme adopted by the invention is that: it is a kind of
High temperature alloy silk material, by mass percentage, chemical component are as follows: Cr 15 ~ 16, Fe 7.5 ~ 8.5, Ti2.5 ~ 2.6, Nb
0.8 ~ 1.0, Al 0.6 ~ 0.9, C £ 0.06, Zr 0.05 ~ 0.08, P £ 0.008, S £ 0.008, surplus Ni.
A kind of preparation method of high temperature alloy silk material, it is characterised in that: include the following steps;
Step 1: vacuum induction melting+electroslag remelting melting duplex is smelted;
Step 2: forging;Forging temperature is at 950 °C ~ 1200 °C, and deformation amount controlling is 50 ~ 80%;By alloy be swaged into 80mm ×
The blank of 80mm × L;
Step 3: solution heat treatment;Solution heat treatment temperature is 1000 °C ~ 1150 °C, keeps the temperature 30 ~ 60 minutes;
Step 4: it is rolled into wire rod;Alloy blank is rolled into the wire rod of 8 ~ 12mm, rolling temperature is at 1000 °C ~ 1150 °C;
Step 5: annealing cold drawing;It is annealed repeatedly cold drawing, number is usually 15 ~ 30 times, and deformation amount controlling per pass is 15
Between ~ 30%;Annealing temperature is 1000 °C ~ 1100 °C, between heat preservation 30 ~ 60 minutes;The cold drawing is to carry out at room temperature
Drawing, drawing velocity 60-100m/min;
Step 6: annealing and pickling;When deflection reaches 30 ~ 40%, annealing and pickling are carried out, removes surface oxide layer, is made and produces
Product.
It is preferred: in cold drawing silk material diameter < 3mm, the method washed using vacuum annealing acid adding, and vacuum degree < 10- 2Pa, annealing temperature are 1000 °C ~ 1100 °C, and the deformation amount controlling between heat preservation 30 ~ 60 minutes between twice annealing is 15 ~ 30%.
It is preferred: the deformation in cold drawing silk material diameter > 3mm, using the method washed of normal pressure annealing acid adding, between twice annealing
Amount control is 30 ~ 40%.
Beneficial effects of the present invention;A kind of high temperature alloy silk material and preparation method thereof, the technique is using annealing, pickling and cold
The method of drawing controls the total deformation of each silk material and the deflection per pass of silk material, reduces inhomogeneous deformation, obtains uniform
The tissue of distribution;As silk material size < 3mm, in addition to the deflection of control silk material, it is also necessary to guarantee silk using vacuum heat treatment
The surface quality of material avoids the occurrence of corrosion and other defect;The even tissue of silk material product of the invention is distributed, no layering or thick
Crystalline substance tissue;The features such as the defects of silk material surface flawless, pockmark has dimensional accuracy high, and surface quality is excellent.
Specific embodiment
In order to be more clear goal of the invention of the invention, technical solution and its advantageous effects, below in conjunction with specific
Embodiment, the present invention will be described in further detail;
A kind of high temperature alloy silk material, by mass percentage, chemical component are as follows: Cr 15 ~ 16, Fe 7.5 ~ 8.5, Ti2.5 ~
2.6, Nb 0.8 ~ 1.0, Al 0.6 ~ 0.9, C £ 0.06, Zr 0.05 ~ 0.08, P £ 0.008, S £ 0.008, surplus Ni.
A kind of preparation method of high temperature alloy silk material, it is characterised in that: include the following steps;
Step 1: vacuum induction melting+electroslag remelting melting duplex is smelted;
Step 2: forging;Forging temperature is at 950 °C ~ 1200 °C, and deformation amount controlling is 50 ~ 80%;By alloy be swaged into 80mm ×
The blank of 80mm × L;
Step 3: solution heat treatment;Solution heat treatment temperature is 1000 °C ~ 1150 °C, keeps the temperature 30 ~ 60 minutes;
Step 4: it is rolled into wire rod;Alloy blank is rolled into the wire rod of 8 ~ 12mm, rolling temperature is at 1000 °C ~ 1150 °C;
Step 5: annealing cold drawing;It is annealed repeatedly cold drawing, number is usually 15 ~ 30 times, and deformation amount controlling per pass is 15
Between ~ 30%;Annealing temperature is 1000 °C ~ 1100 °C, between heat preservation 30 ~ 60 minutes;The cold drawing is to carry out at room temperature
Drawing, drawing velocity 60-100m/min;
Step 6: annealing and pickling;When deflection reaches 30 ~ 40%, annealing and pickling are carried out, removes surface oxide layer, is made and produces
Product.
In cold drawing silk material diameter < 3mm, the method washed using vacuum annealing acid adding, and vacuum degree < 10-2Pa, annealing temperature
Degree is 1000 °C ~ 1100 °C, and the deformation amount controlling between heat preservation 30 ~ 60 minutes between twice annealing is 15 ~ 30%;In cold-drawn wire
When material diameter > 3mm, using the method washed of normal pressure annealing acid adding, the deformation amount controlling between twice annealing is 30 ~ 40%.
Specific implementation of the invention: containing a large amount of S and P element in GH4145 alloy, these harmful elements will form folder
Sundries, when influencing the temperature-room type plasticity of alloy, especially silk material diameter < 1mm, some big sulfide will cause fracture of wire, therefore close
It must be strictly controlled P the and S element in alloy in golden fusion process, P £ 0.008, S in alloy controlled by two-link smelting process
£ 0.008 improves alloy in addition, vacuum induction+electroslag remelting duplex technique can also reduce loose in alloy and hole quantity
Hot-working character.
The forging of GH4145 alloy and course of hot rolling are the wire rods in order to prepare cold drawing silk material, and forging temperature selection exists
Between 1000 °C ~ 1180 °C, as-forged microstructure uniformity can be effectively improved, removal residual cast sturcture, folding, streamline have some setbacks,
The forging defects such as vortex, percolation, crackle and forging burning;Hot-rolled temperature selects between 1000 °C ~ 1150 °C, can further mention
The structural homogenity of high wire rod.
In cold drawing annealing process, as GH4145 alloy disc size > 3mm, annealed using normal pressure, annealing temperature is
Between 1000 °C ~ 1100 °C, heat preservation 30 ~ 60 minutes;Then pickling is carried out using mixed acid, removes the oxide skin on surface;Work as silk
When material size < 3mm, using vacuum annealing;Cost has been saved while preparing qualified products in this way.
In cold drawing annealing process, as silk material diameter > 3mm, moderate finite deformation amount 30 ~ 40% is used between twice annealing, is improved
The storage energy of alloy deformation process is conducive to that perfect recrystallization occurs, controls the structural homogenity of silk material.As silk material diameter < 3mm
When, using compared with small deformation amount 15 ~ 30% between twice annealing, in case overprocessing hardening will affect the surface quality of silk material.
The ingredient of alloy of the present invention is shown in Table 1, and the S content in two kinds of GH4145 alloys is significantly different.One kind is 0.009%, separately
One kind is 0.0008%, the former is subsequent 10 times, and two kinds of alloys are all made of vacuum induction melting+electroslag remelting melting duplex smelting
Refining, obtains the ESR ingot of diameter 360mm, then 1180 °C of squares for being swaged into 50mm × 50mm, after figuring of surface, in 1100 °C of hot rollings
At the wire rod of 8mm, the wire rod of 8mm is annealed 30 minutes at 1080 °C, then pickling.
Embodiment 1
Select alloying component for the GH4145 alloy of high S content, the process route of use is shown in Table 2;It was found that as silk material < 1.5mm,
Silk material is easy to fracture of wire in cold drawing process;Show that this is related with the higher S content in alloy;Therefore, in embodiment 2-4
The alloying component of use is low S content alloy.
Embodiment 2
The alloying component of selection is low S content alloy, and the process route of use is shown in Table 3;After the S content for reducing alloy, alloy
Cold drawing performance improve very much, occur during the experiment without fracture of wire situation;The surface quality of product;It was found that finished product silk material surface
There is etch pit, illustrate that pickling effect is bad, needs to carry out vacuum heat treatment in crin.
Embodiment 3
The alloying component of selection is low S content alloy, and the process route of use is shown in Table 4;It was found that finished product silk material surface is good, it is transversal
Covering weave observation shows that Tissue distribution is uniform.
Embodiment 4
The alloying component of selection is low S content alloy, and the process route of use is shown in Table 5;The surface quality of product is excellent, cross section
Structure observation shows that Tissue distribution is uneven.
The chemical component of 1 GH4145 alloy of table
Element | Cr | Fe | Ti | Nb | Al | C | Zr | B | Si | P | S | Ni |
High S | 15.8 | 8.0 | 2.63 | 1.1 | 0.83 | 0.03 | 0.06 | 0.006 | 0.12 | 0.01 | 0.009 | Surplus |
Low S | 15.0 | 8.0 | 2.47 | 1.0 | 0.7 | 0.03 | 0.06 | 0.006 | 0.08 | 0.007 | 0.0008 | Surplus |
The working process parameter of 2 embodiment 1 of table
The working process parameter of 3 embodiment 2 of table
The working process parameter of 4 embodiment 3 of table
The working process parameter of 5 embodiment 4 of table
Above-described embodiment is only intended to clearly illustrate description made by the present invention, and does not limit the embodiments, for
For those skilled in the art, other different forms of changes or modifications may be made based on the above description,
There is no necessity and possibility to exhaust all the enbodiments, and thus changes and variations that derived from are still
Among protection scope of the present invention.
Claims (4)
1. a kind of high temperature alloy silk material, by mass percentage, chemical component are as follows: Cr 15 ~ 16, Fe 7.5 ~ 8.5, Ti2.5
~ 2.6, Nb 0.8 ~ 1.0, Al 0.6 ~ 0.9, C £ 0.06, Zr 0.05 ~ 0.08, P £ 0.008, S £ 0.008, surplus are
Ni。
2. a kind of preparation method of high temperature alloy silk material, it is characterised in that: include the following steps;
Step 1: vacuum induction melting+electroslag remelting melting duplex is smelted;
Step 2: forging;Forging temperature is at 950 °C ~ 1200 °C, and deformation amount controlling is 50 ~ 80%;By alloy be swaged into 80mm ×
The blank of 80mm × L;
Step 3: solution heat treatment;Solution heat treatment temperature is 1000 °C ~ 1150 °C, keeps the temperature 30 ~ 60 minutes;
Step 4: it is rolled into wire rod;Alloy blank is rolled into the wire rod of 8 ~ 12mm, rolling temperature is at 1000 °C ~ 1150 °C;
Step 5: annealing cold drawing;It is annealed repeatedly cold drawing, number is usually 15 ~ 30 times, and deformation amount controlling per pass is 15
Between ~ 30%;Annealing temperature is 1000 °C ~ 1100 °C, between heat preservation 30 ~ 60 minutes;The cold drawing is to carry out at room temperature
Drawing, drawing velocity 60-100m/min;
Step 6: annealing and pickling;When deflection reaches 30 ~ 40%, annealing and pickling are carried out, removes surface oxide layer, is made and produces
Product.
3. a kind of preparation method of high temperature alloy silk material according to claim 2, it is characterised in that: in cold drawing silk material diameter
When < 3mm, the method washed using vacuum annealing acid adding, and vacuum degree < 10-2Pa, annealing temperature are 1000 °C ~ 1100 °C, are protected
Deformation amount controlling between temperature 30 ~ 60 minutes between twice annealing is 15 ~ 30%.
4. a kind of preparation method of high temperature alloy silk material according to claim 2, it is characterised in that: in cold drawing silk material diameter
When > 3mm, using the method washed of normal pressure annealing acid adding, the deformation amount controlling between twice annealing is 30~40%.
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Cited By (6)
Publication number | Priority date | Publication date | Assignee | Title |
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CN110760716A (en) * | 2019-10-22 | 2020-02-07 | 南京达迈科技实业有限公司 | Nickel-yttrium alloy wire for spark plug electrode material and preparation method thereof |
CN111304567A (en) * | 2020-03-16 | 2020-06-19 | 江苏集萃先进金属材料研究所有限公司 | Method for producing GH4169 fine-grained bar through thermomechanical treatment |
CN111910104A (en) * | 2020-07-14 | 2020-11-10 | 上海康晟航材科技股份有限公司 | Economical nickel-chromium-based high-temperature alloy for hydrogen fuel cell air compressor and foil thereof |
WO2021007915A1 (en) * | 2019-06-26 | 2021-01-21 | 江苏省沙钢钢铁研究院有限公司 | Superfine extra-high-strength steel wire, steel wire rod, and production method of the steel wire rod |
CN112323000A (en) * | 2020-11-13 | 2021-02-05 | 西南铝业(集团)有限责任公司 | Method for eliminating coarse crystal ring of alloy extrusion product |
CN115106796A (en) * | 2022-06-28 | 2022-09-27 | 中航上大高温合金材料股份有限公司 | Production process of GH6159 alloy large-size cold-drawn bar |
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CN111304567A (en) * | 2020-03-16 | 2020-06-19 | 江苏集萃先进金属材料研究所有限公司 | Method for producing GH4169 fine-grained bar through thermomechanical treatment |
CN111910104A (en) * | 2020-07-14 | 2020-11-10 | 上海康晟航材科技股份有限公司 | Economical nickel-chromium-based high-temperature alloy for hydrogen fuel cell air compressor and foil thereof |
CN112323000A (en) * | 2020-11-13 | 2021-02-05 | 西南铝业(集团)有限责任公司 | Method for eliminating coarse crystal ring of alloy extrusion product |
CN115106796A (en) * | 2022-06-28 | 2022-09-27 | 中航上大高温合金材料股份有限公司 | Production process of GH6159 alloy large-size cold-drawn bar |
CN115106796B (en) * | 2022-06-28 | 2024-01-23 | 中航上大高温合金材料股份有限公司 | GH6159 alloy large-size cold-drawn bar production process |
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Application publication date: 20190308 |