CN106756683A - Heating means before a kind of deformation of GH4169 alloys - Google Patents
Heating means before a kind of deformation of GH4169 alloys Download PDFInfo
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- CN106756683A CN106756683A CN201611096345.7A CN201611096345A CN106756683A CN 106756683 A CN106756683 A CN 106756683A CN 201611096345 A CN201611096345 A CN 201611096345A CN 106756683 A CN106756683 A CN 106756683A
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- 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
The invention provides heating means before a kind of deformation of GH4169 alloys, middle temperature insulation after first stage heating is carried out to the GH4169 alloys, carry out second stage heating to the alloy after the middle temperature insulation carries out soak again；The temperature of the middle temperature insulation is 880~920 DEG C, and the temperature of the soak is 1000~1045 DEG C.The method that the present invention is provided, is heated to GH4169 alloys using two-part, and compared with prior art, the heat time is only the 2/3 of conventional Three-section type heating time, and the efficiency of heating surface is improved；Using 880~920 DEG C of heating-up temperatures as the insulation of middle temperature, it is to avoid separate out overlapping for peak temperature with δ phases, the control to δ phase morphologies is realized, improve structural homogenity.
Description
Technical field
The present invention relates to heating side before GH4169 Alloy Processings field, more particularly to a kind of deformation of GH4169 alloys
Method.
Background technology
High temperature alloy is to refer to bear larger complex stress more than 600 DEG C, and the high alloy with surface stability
Change iron-based, niobium base or cobalt-based austenitic metal material.High temperature alloy is with its good elevated temperature strength and anti-oxidant, anticorrosive, anti-
Fatigue, creep resistant, Resisting fractre and structure stability are widely used in Aeronautics and Astronautics and navigational field.
GH4169 alloys are a kind of alloying level high temperature alloys higher, are the high temperature alloys being most widely used.But
It is GH4169 alloy hot poor-performings, needs to heat it before GH4169 alloy machining deformations, ensures
GH4169 alloys have good plasticity in deformation after unloading process, so as to obtain required forging's block dimension, structural state
And performance.
Mode of heating is Three-section type heating before existing GH4169 alloy deformations processing.Such as Chinese patent
CN103465027A discloses a kind of GH4169 alloys fine grain disk base manufacture method, specifically discloses using at three sections of mode of heatings
Reason blank, is heated in the way of 845~855 DEG C, 980~990 DEG C, 1015~1025 DEG C of three sections of heating to blank；For another example
Chinese patent CN103447768A discloses a kind of preparation method of GH4169 alloy large-sizes abnormity interface ring billet, and specific disclosure will
GH4169 alloys are heated to 985 DEG C after being heated to 850 DEG C, be heated to 1100 ± 10 DEG C of three sections of mode of heatings, are follow-up change
Shape processing provides stabilizing tissue.But in existing Three-section type heating specification, middle temperature holding temperature is generally between 940~985 DEG C,
The peak temperature that this temperature is separated out close to δ phases, is incubated at this temperature for a long time, inevitably results in δ phase morphologies and distribution does not conform to
It is suitable, cause the component segregation of microcell in alloy, cause forging performance heterogeneity.As can be seen here, heating rule before rational forging are formulated
Important step during model under forging technology.
The content of the invention
In view of this, it is an object of the invention to provide heating means before a kind of deformation of GH4169 alloys, it is possible to increase
Obtain the structural homogenity of alloy product.
In order to realize foregoing invention purpose, the present invention provides following technical scheme：
Heating means before a kind of deformation of GH4169 alloys, it is characterised in that first is carried out to the GH4169 alloys
Middle temperature insulation after stepwise heating, carry out second stage heating to the alloy after the middle temperature insulation carries out soak again；It is described
The temperature of middle temperature insulation is 880~920 DEG C, and the temperature of the soak is 1000~1045 DEG C.
Preferably, the heating rate of the first stage heating is 1.0~3.0 DEG C/min；The second stage heating
Heating rate is 1.3~2.0 DEG C/min.
Preferably, the temperature that the content setting middle temperature according to niobium element in the GH4169 alloys is incubated；
When niobium element in the GH4169 alloys content for [4.75wt%, 5.0wt%) when, the temperature that the middle temperature is incubated
Spend for [880 DEG C, 895 DEG C)；
When niobium element in the GH4169 alloys content for [5.0wt%, 5.2wt%) when, the temperature that the middle temperature is incubated
Spend for [895 DEG C, 907 DEG C)；
When the content of niobium element in the GH4169 alloys is [5.2wt%, 5.5wt%], the temperature of the middle temperature insulation
Spend is [907 DEG C, 920 DEG C].
Preferably, the temperature of the middle temperature insulation determines according to following steps：
The temperature range of the middle temperature insulation of default GH4169 alloys, the temperature range of the default middle temperature insulation is 800
~960 DEG C；
Isothermal holding is carried out to the GH4169 alloys within the scope of the default temperature；
Structure observation is carried out to GH4169 alloys after the isothermal holding；
According to the result of the structure observation, the temperature of the middle temperature insulation is obtained；
When the result of the structure observation meets middle temperature insulation organizational requirements, the temperature of the result is obtained for middle temperature is protected
The temperature of temperature；The middle temperature is incubated organizational requirements：There is no mixed crystal, the percent by volume of δ phases is the pattern of 5%~10%, δ phases
It is corynebacterium, the length-width ratio of δ phases is 2~3.
Preferably, temperature to be tested is chosen by gradient within the temperature range of the default middle temperature insulation；The temperature
Gradient is 5~10 DEG C.
Preferably, the content of the niobium element in the GH4169 alloys sets the temperature of the soak；
When niobium element in the GH4169 alloys content for [4.75wt%, 5.0wt%) when, the temperature of the soak
Spend for [1000 DEG C, 1015 DEG C)；
When niobium element in the GH4169 alloys content for [5.0wt%, 5.2wt%) when, the temperature of the soak
Spend for [1015 DEG C, 1030 DEG C)；
When the content of niobium element in the GH4169 alloys is [5.2wt%, 5.5wt%], the temperature of the soak
Spend is [1030 DEG C, 1045 DEG C].
Preferably, the temperature of the soak determines according to following steps：
The temperature range of the soak of default GH4169 alloys, the temperature range of the default soak is 970
~1070 DEG C；
Isothermal holding is carried out to the GH4169 alloys within the scope of the default temperature；
Structure observation is carried out to the GH4169 alloys after the isothermal holding；
According to the result of the structure observation, the temperature of the soak is obtained；
When the result of the structure observation meets high-temperature heating organizational standard, the temperature for obtaining the result is high temperature dwell
The temperature of temperature；The soak organizational requirements are：There is no a mixed crystal, the percent by volume of δ phases is for the pattern of 0~2%, δ phases
Graininess, the length-width ratio of δ phases is 1~1.2.
Preferably, test temperature is chosen by gradient within the temperature range of the default soak；The temperature ladder
Spend is 5~10 DEG C.
The invention provides heating means before a kind of deformation of GH4169 alloys, the first rank is carried out to the GH4169 alloys
Middle temperature insulation after Duan Jiare, carry out second stage heating to the alloy after the middle temperature insulation carries out soak again；In described
The temperature of temperature insulation is 880~920 DEG C, and the temperature of the soak is 1000~1045 DEG C.The method that the present invention is provided is right
GH4169 alloys are heated using two-part, and compared with prior art, the heat time is only the 2/3 of conventional Three-section type heating time,
The efficiency of heating surface is improved；Using 880~920 DEG C of heating-up temperatures as the insulation of middle temperature, it is to avoid using the weight that peak temperature is separated out with δ phases
Close, realize the control to the form of δ phases, improve structural homogenity.The result of embodiment shows, using two-part mode of heating energy
Enough reach the identical equal temperature time with Three-section type heating mode, it is seen that on the premise of the shortening heat time raising efficiency of heating surface still
Can ensure that heating effect；GH4169 alloys are heated using technical scheme, without mixed in being organized
Brilliant appearance, and grain boundaries precipitated phase is few, and precipitated phase length-width ratio is controlled in the range of 1~1.2, uniform texture.
Further, the different niobium element contents according to GH4169 alloys limit the temperature and high temperature of different middle temperature insulations
Holding temperature, it is to avoid using the mode of heating lumped together, take into full account niobium element content to the second precipitated phase δ in heating process
The influence of the content and pattern of phase, obtains suitable δ phases content and δ phase morphology features, while avoiding the big of Grain-Boundary Phase precipitation
The segregation of the niobium element caused by the δ phases of amount, and then control structural homogenity.
Brief description of the drawings
The present invention is further detailed explanation with reference to the accompanying drawings and detailed description.
Fig. 1 is the heating procedure figure of comparative example of the present invention 1；
Fig. 2 is the alloy structure shape appearance figure that comparative example of the present invention 1 is obtained；
Fig. 3 is tissue topography figure of the Nb alloys high after insulation under the conditions of 890 DEG C in the embodiment of the present invention 1；
Tissue topography after Fig. 4 is incubated for the middle Nb alloys of the embodiment of the present invention 1 under the conditions of 895 DEG C schemes；
Tissue topography after Fig. 5 is incubated for the low Nb alloys in the embodiment of the present invention 1 under the conditions of 909 DEG C schemes；
Fig. 6 is tissue topography figure of the Nb alloys high after insulation under the conditions of 1012 DEG C in the embodiment of the present invention 2；
Tissue topography after Fig. 7 is incubated for the middle Nb alloys in the embodiment of the present invention 2 under the conditions of 1020 DEG C schemes；
Tissue topography after Fig. 8 is incubated for the low Nb alloys in the embodiment of the present invention 2 under the conditions of 1030 DEG C schemes；
Fig. 9 is the heating procedure figure of the embodiment of the present invention 3；
Figure 10 is the alloy structure shape appearance figure that the embodiment of the present invention 3 is obtained；
Figure 11 is the heating procedure figure of the embodiment of the present invention 4；
Figure 12 is the alloy structure shape appearance figure that the embodiment of the present invention 4 is obtained；
Figure 13 is the heating procedure figure of the embodiment of the present invention 5；
Figure 14 is the alloy structure shape appearance figure that the embodiment of the present invention 5 is obtained.
Specific embodiment
The invention provides the heating means before a kind of deformation of GH4169 alloys, first is carried out to the GH4169 alloys
Middle temperature insulation after stepwise heating, carry out second stage heating to the alloy after the middle temperature insulation carries out soak again；It is described
The temperature of middle temperature insulation is 880~920 DEG C, and the temperature of the soak is 1000~1045 DEG C.
The method that the present invention is provided, two-part mode of heating is used to GH4169 alloys, and the heat time is only conventional three sections
The 2/3 of formula heat time, the efficiency of heating surface is improved；Using 880~920 DEG C of heating-up temperatures as the insulation of middle temperature, it is to avoid use and δ phases
The coincidence of peak temperature is separated out, the control to the form of δ phases is realized, structural homogenity is improved.
The GH4169 alloys are carried out middle temperature insulation by the present invention first, and the temperature of the middle temperature insulation is 880~920
℃.The present invention does not have particular/special requirement to the component of the GH4169 alloys, using GH4169 well-known to those skilled in the art
Alloy；In the present invention, the GH4169 alloys by weight percentage, including following components：0~0.08% C,
17.0%~21.0% Cr, 50.0%~55.0% Ni ,≤1.0% Co, 2.80%~3.30% Mo, 0.30%~
0.70% Al, 0.75%~1.15% Ti, 4.75%~5.50%Nb, the Fe of surplus.In the present invention, the GH4169
Alloy is preferably bar-shaped or sheet material.The no particular/special requirement in source to the GH4169 alloys of the invention, using art technology
GH4169 alloys known to personnel.
In order to determine the temperature that the middle temperature is incubated, the present invention preferably first presets the middle temperature insulation of GH4169 alloys to the present invention
Temperature range, the default middle temperature holding temperature scope be 800~960 DEG C；
Isothermal holding is carried out to the GH4169 alloys within the scope of the default temperature；
Structure observation is carried out to GH4169 alloys after the isothermal holding；
According to the result of the structure observation, the temperature of the middle temperature insulation is obtained；
When the result of the structure observation meets middle temperature insulation to be organized as requiring, the temperature for obtaining the result is middle temperature
The temperature of insulation；The organizational requirements of the middle temperature insulation are：There is no mixed crystal, the percent by volume of δ phases is 5%~10%, δ phases
Pattern is corynebacterium, and the length-width ratio of δ phases is 2~3.
In the present invention, the temperature range of the default middle temperature insulation is preferably 800~960 DEG C.In the present invention, institute
The temperature range for stating middle temperature insulation is preferably the temperature range that the middle temperature of conventional Three-section type heating mode is incubated.
After the temperature range of the middle temperature insulation of default GH4169 alloys, the present invention is within the scope of the default temperature to institute
Stating GH4169 alloys carries out isothermal holding.In order to preferably filter out effect preferably temperature, the present invention is preferably described default
Middle temperature insulation within the temperature range of take different temperature.The present invention chooses test temperature preferably in the temperature range by gradient
Degree；In the present invention, the thermograde is preferably 5~10 DEG C, more preferably more preferably 6~9 DEG C, 7~8 DEG C.This
Invention is preferably the size of heated alloy and multiplying for soaking time coefficient in the time of the default temperature range inside holding
Product；In the present invention, the heat insulating coefficient of the middle temperature insulation is preferably 8min/10mm.In the present invention, the middle temperature was incubated
The alloy of journey is GH4169 alloy raw materials, and its size is preferably determined with the shape of the GH4169 alloys：When the GH4169 is closed
When gold is for sheet material, the size of the heated alloy is the thickness of the sheet material；It is described when the GH4169 alloys are bar
The size for being heated alloy is the diameter of the bar；When the GH4169 alloys are irregular shape, the heated conjunction
The size of gold is the size in the most thick direction of the irregular shape.
To the GH4169 alloys after isothermal holding under the conditions of different test temperatures, at insulation described in preferred pair of the present invention
GH4169 alloys after reason carry out structure observation after being cooled down.In the present invention, the temperature after the cooling is preferably room temperature,
More preferably 20~25 DEG C.The present invention does not have particular/special requirement to the type of cooling, ripe using those skilled in the art institute
The type of cooling known, in an embodiment of the present invention, the cooling is specially water-cooled.The present invention is to the structure observation
Mode does not have particular/special requirement, using structure observation mode well-known to those skilled in the art；In embodiments of the invention
In, it is specific that structure observation is carried out to the GH4169 alloys using light microscope.
After completing the structure observation, the present invention is set in being carried out to the GH4169 alloys according to obtaining observing result
The temperature of temperature insulation.Specifically, in the present invention, when the result of the structure observation meets middle temperature insulation organizational standard, will
Corresponding isothermal holding temperature is set as the temperature of middle temperature insulation.In the present invention, the organizational requirements of the middle temperature insulation are preferred
For：There is no a mixed crystal, the percent by volume of δ phases is corynebacterium for the pattern of 5%~10%, δ phases, and the length-width ratio of δ phases is 2~3.This
Invent in the organizational requirements of the middle temperature insulation, the percent by volume of the δ phases is more preferably 6%~9%, more preferably
7%~8%；In the organizational requirements of middle temperature insulation of the present invention, the length-width ratio of the δ phases is more preferably 2.2~2.8,
More preferably 2.5~2.6.
The present invention chooses different test temperatures within the temperature range of the middle temperature insulation for being limited, in different test temperature
Middle temperature isothermal holding is carried out under the conditions of degree to the GH4169 alloys, is determined according to organizational standard conjunctive tissue observation result optimal
Middle temperature insulation temperature, realize the control to Second Phase Precipitation in heating process.
In the present invention, the temperature of the middle temperature insulation is 880~920 DEG C.The present invention is preferably closed according to the GH4169
The temperature of the content setting of the niobium element middle temperature insulation in gold：
When niobium element in the GH4169 alloys content for [4.75wt%, 5.0wt%) when, the temperature that the middle temperature is incubated
Degree be preferably [880 DEG C, 895 DEG C), more preferably 885 DEG C~890 DEG C；
When niobium element in the GH4169 alloys content for [5.0wt%, 5.2wt%) when, the temperature that the middle temperature is incubated
Degree be preferably [895 DEG C, 907 DEG C), more preferably 900 DEG C~905 DEG C；
When the content of niobium element in the GH4169 alloys is [5.2wt%, 5.5wt%], the temperature of the middle temperature insulation
Degree is preferably [907 DEG C, 920 DEG C], more preferably 910 DEG C~915 DEG C.
The present invention limits the GH4169 alloys of different niobium element contents the temperature of different middle temperature insulations, it is to avoid use one
Mode of heating in general, takes into full account niobium element content to the content of the second precipitated phase δ phases in heating process and pattern
Influence, obtain suitable δ phases content and δ phase morphology features, while avoid Grain-Boundary Phase separate out substantial amounts of δ phases caused by niobium unit
The segregation of element, and then control structural homogenity.
In the present invention, first stage heating preferably is selected from 750 DEG C and is heated up, and reaches the temperature that the middle temperature is incubated
Degree.In the present invention, the heating rate of the first stage heating is preferably 1.0~3.0 DEG C/min, more preferably 1.2
~2.7 DEG C/min, more preferably 1.5~2.2 DEG C/min.The present invention does not have special wanting to the control mode of the heating rate
Ask, using the control mode of heating rate well-known to those skilled in the art；Embodiments of the invention are specifically used and added
The 80~90% of thermal instrument general power are heated, and more preferably 86~88%.The present invention is to the heating instrument total work
Rate does not have particular/special requirement, using well-known to those skilled in the art for GH4169 alloys heating instrument general power.
In the present invention, under the ramp rate conditions, successfully avoid the rate of heat addition in traditional heating mode it is too fast when,
Forging internal temperature field is uneven, it is possible that the defect such as discontented, crackle of filling during deformation after unloading after the completion of heating；Together
Sample avoids that the rate of heat addition is excessively slow, causes coarse-grain occur inside the blank after heating, once the deflection in deformation process is not enough
In making the tissue of coarse-grain perfect recrystallization, the deformation of final molding there is defect, quality will affected problem.
In the present invention, the soaking time of the middle temperature holding stage is preferably the size and soaking time of heated alloy
The product of coefficient；In the present invention, the heat insulating coefficient of the middle temperature insulation is preferably 8min/10mm.In the present invention, in described
The heated alloy of warm holding stage is GH4169 alloy raw materials, and its size is preferably determined with the shape of the GH4169 alloys：
When the GH4169 alloys are sheet material, the size of the heated alloy is the thickness of the sheet material；When the GH4169 is closed
When gold is for bar, the size of the heated alloy is the diameter of the bar；When the GH4169 alloys are irregular shape
When, the size of the heated alloy is the size in the most thick direction of the irregular shape.
Temperature in order to determine the soak of the invention, the present invention preferably first presets the soak of GH4169 alloys
Temperature range, the default soak temperature range be 970~1070 DEG C；
Isothermal holding is carried out to the GH4169 alloys within the scope of the default temperature；
Structure observation is carried out to GH4169 alloys after the isothermal holding；
According to the result of the structure observation, the temperature of the soak is obtained；
When the result of the structure observation meets the requirement of soak organizational standard, it is height to obtain the temperature of the result
The temperature of temperature insulation；The organizational requirements of the soak are：There is no mixed crystal, the percent by volume of δ phases is 0~2%, δ phases
Pattern is graininess, and the length-width ratio of δ phases is 1~1.2.
In the present invention, the temperature range of the default soak is preferably 970~1070 DEG C.In the present invention,
The soak temperature range is preferably the high-temperature heating temperature range of conventional Three-section type heating mode.
After the temperature range of the soak of default GH4169 alloys, the present invention is within the scope of the default temperature to institute
Stating GH4169 alloys carries out isothermal holding.In order to preferably filter out effect preferably temperature, the present invention is preferably in the height for obtaining
Different temperature are taken in the range of warm holding temperature.The present invention chooses test temperature preferably in the temperature range by gradient；
In the present invention, the thermograde is preferably 5~10 DEG C, more preferably more preferably 6~9 DEG C, 7~8 DEG C.The present invention exists
The time being incubated within the temperature range of the acquisition is preferably the size of heated alloy and the product of soaking time coefficient；At this
In invention, the heat insulating coefficient of the soak is preferably 8min/10mm.In the present invention, the quilt of the middle temperature holding stage
Heating alloy is GH4169 alloy raw materials, and its size is preferably determined with the shape of the GH4169 alloys：When the GH4169 is closed
When gold is for sheet material, the size of the heated alloy is the thickness of the sheet material；It is described when the GH4169 alloys are bar
The size for being heated alloy is the diameter of the bar；When the GH4169 alloys are irregular shape, the heated conjunction
The size of gold is the size in the most thick direction of the irregular shape.
To the GH4169 alloys after isothermal holding under the conditions of different test temperatures, at insulation described in preferred pair of the present invention
GH4169 alloys after reason carry out structure observation after being cooled down.The present invention to the type of cooling preferably as described above
Scheme is carried out, and be will not be repeated here.The present invention does not have particular/special requirement to the mode of the structure observation, using people in the art
Structure observation mode known to member；In an embodiment of the present invention, it is specific to use light microscope to the GH4169
Alloy carries out structure observation.
After completing the structure observation, observation result of the present invention according to obtained by, setting is entered to the GH4169 alloys
The temperature of row soak.Specifically, in the present invention, when the observation result of the tissue meets soak organizational requirements
When, corresponding isothermal holding temperature is set as the temperature of soaking period.In the present invention, the soak tissue will
Ask preferably：There is no a mixed crystal, the percent by volume of δ phases is graininess shape for the pattern of 0~2%, δ phases, and the length-width ratio of δ phases is 1
~1.2.In soak organizational requirements of the present invention, the percent by volume of the δ phases is more preferably 0.2%~
0.8%, more preferably 0.5%~0.6%；In soak organizational requirements of the present invention, the length-width ratio of the δ phases is further
Preferably 1.02~1.08, more preferably 1.05.
The present invention chooses different test temperatures within the temperature range of the soak for being limited, in different test temperature
The isothermal holding of hot stage is carried out under the conditions of degree to the GH4169 alloys, it is true according to organizational standard conjunctive tissue observation result
The temperature of fixed optimal soak, realizes the control to Second Phase Precipitation in heating process.
The present invention determines the temperature of soak according to above-mentioned technical proposal.In the present invention, the temperature of the soak
Spend is 1000~1045 DEG C.
Content of the present invention preferably according to niobium element in the GH4169 alloys sets the temperature of the soak：Work as institute
State the content of niobium element in GH4169 alloys for [4.75wt%, 5.0wt%) when, the temperature of the soak is preferably
[1000 DEG C, 1015 DEG C), more preferably 1005 DEG C~1012 DEG C, more preferably 1008 DEG C~1010 DEG C；When described
In GH4169 alloys the content of niobium element for [5.0wt%, 5.2wt%) when, the temperature of the soak is preferably [1015
DEG C, 1030 DEG C), more preferably 1020 DEG C~1028 DEG C, most preferably 1025 DEG C；When niobium element in the GH4169 alloys
Content be [5.2wt%, 5.5wt%] when, the temperature of the soak is preferably [1030 DEG C, 1045 DEG C], further it is excellent
Elect 1032 DEG C~1042 DEG C, most preferably more preferably 1035 DEG C~1040 DEG C, 1038 DEG C as.The present invention contains to different niobium elements
The GH4169 alloys of amount limit the temperature of different soaks, it is to avoid using the mode of heating lumped together, take into full account niobium
Influence of the constituent content to the content and pattern of the second precipitated phase δ phases in heating process, obtains suitable δ phases content and δ phases
Shape characteristic, at the same avoid Grain-Boundary Phase separate out substantial amounts of δ phases caused by niobium element segregation, and then control even tissue
Property.
The present invention carries out second stage heating and carries out soak again to the alloy after the middle temperature insulation；In the present invention
In, the temperature that the second stage heating preferably is selected from the middle temperature insulation is heated up, and reaches the temperature of the soak.
In the present invention, the time interval of the first stage heating and middle temperature insulating process and second stage heating and soak process
It is 0, i.e., carries out middle temperature insulation after described first stage heating, second stage heating is directly carried out after completing the middle temperature insulation.
In the present invention, the first stage heats and middle temperature insulating process is heated with second stage and soak process is preferably in phase
Carried out in same heating furnace.
In the present invention, the heating rate of the second stage heating is preferably 1.3~2.0 DEG C/min, further preferably
It is 1.3~1.7 DEG C/min, more preferably 1.4~1.6 DEG C/min.The present invention is to the control mode of the heating rate without spy
It is different to require, using the control mode of heating rate well-known to those skilled in the art；Embodiments of the invention are specifically adopted
Heated with the 75~85% of heating instrument general power, more preferably 78~80%.The present invention is to the heating instrument
General power does not have particular/special requirement, is for GH4169 alloy heating instrument general powers using well-known to those skilled in the art
Can.
In the present invention, the restriction of the heating rate of the second stage heating equally successfully avoid traditional heating mode
When the middle rate of heat addition is too fast, forging internal temperature field is uneven, it is possible that filling during deformation after unloading after the completion of heating
The defects such as discontented, crackle；While avoiding, the rate of heat addition is excessively slow, cause coarse-grain occur inside the blank after heating, once deformation
During deflection be not enough to make the tissue of coarse-grain perfect recrystallization, the deformation of final molding there is defect, quality will
Affected problem.
In the present invention, the soaking time of the soak is preferably the size and soaking time coefficient of heated alloy
Product；In the present invention, the heat insulating coefficient of the soak is preferably 6min/10mm.In the present invention, the high temperature dwell
The heated alloy of thermophase is GH4169 alloy raw materials, and its size is preferably determined with the shape of the GH4169 alloys：Work as institute
When stating GH4169 alloys for sheet material, the size of the heated alloy is the thickness of the sheet material；When the GH4169 alloys are
During bar, the size of the heated alloy is the diameter of the bar；When the GH4169 alloys are irregular shape, institute
The size for stating heated alloy is the size in the most thick direction of the irregular shape.
The present invention does not have particular/special requirement to the mode of heating of the middle temperature insulation and soak, using people in the art
Mode of heating known to member.In an embodiment of the present invention, it is specific to be carried out by the way of heating is heat-treated.In this hair
In bright, the interlude of the middle temperature heating and high-temperature heating is preferably 0~5min, more preferably 0.5~2min.
The invention provides the heating means before a kind of deformation of GH4169 alloys, first is carried out to the GH4169 alloys
Middle temperature insulation after stepwise heating, carry out second stage heating to the alloy after the middle temperature insulation carries out soak again；It is described
The temperature of middle temperature insulation is 880~920 DEG C, and the temperature of the soak is 1000~1045 DEG C.The method that the present invention is provided,
Two-part mode of heating is used to GH4169 alloys, the heat time is only the 2/3 of conventional Three-section type heating time, and the efficiency of heating surface is carried
It is high；Using 880~920 DEG C of heating-up temperatures as the insulation of middle temperature, it is to avoid separate out overlapping for peak temperature using with δ phases, realize to δ
The control of the form of phase, improves structural homogenity.
Heating means before the deformation of the GH4169 alloys provided the present invention with reference to embodiment are carried out specifically
It is bright, but they can not be interpreted as limiting the scope of the present invention.
Nb alloys (4.75~5.0%) high are divided into according to Nb contents in GH4169 alloys, middle Nb alloys (5.0~
5.2%) with low Nb alloys (5.2~5.5%).Component alloy described in table 1 is heated.
1 three kinds of GH4169 alloy compositions of table
Comparative example 1
Niobium alloy A high, middle niobium alloy B and low niobium alloy C are taken, according to the flow chart shown in Fig. 1, these three alloys is carried out
Three-section type heating treatment, and Observation of Histological Structure is carried out to the alloy after heating, as shown in Figure 2, wherein a is height to observation result
Tissue topography's figure of niobium alloy A, b is tissue topography's figure of middle niobium alloy, and c is tissue topography's figure of low niobium alloy, is amplification
200 times of tissue topography's figures.And it is simulated using finite element software, it can be deduced that：Terminate to finally from the insulation of middle temperature
Bar integrally reach a high temperature heating target temperature equal temperature time for 70min, heating total time is 548min.Nb wherein high is closed
Tissue topography's figure of gold occur in that crystallite dimension differ greatly, mixed crystal size it is big, the situation of the wide serious uneven microstructure of scope.
Locally there is strip big crystal grain in the tissue topography of middle Nb alloys, and remainder Tissue distribution is more uniform.The group of low Nb alloys
Pattern is knitted, as can be seen from the figure local distribution has strip crystal grain, distribution is more uniform, but based on strip crystal grain and other crystal grain
Difference, deposit the possibility for occurring serious mixed crystal after deformation.
Embodiment 1
By three kinds of bars of difference Nb contents, bar specification is 220 × 360mm of Φ, and choosing core tissue carries out tissue sight
Examine.Different Nb contents, choose middle temperature holding temperature in the range of 800~960 DEG C, wherein the middle temperature temperature of Nb alloys high is
850 DEG C and 890 DEG C；The middle temperature temperature of middle Nb alloys is 895 DEG C and 890 DEG C, and the middle temperature temperature of low Nb alloys is 909 DEG C and 900
DEG C, soaking time is obtained by diameter of rod with the product of heat insulating coefficient 8min/10mm, is 176min.Complete middle temperature insulation
Afterwards, the tissue result to various sample is observed, under the conditions of 890 DEG C Nb alloys high amplify 500 times tissue as shown in figure 3,
Middle Nb alloys amplify 500 times of tissue as shown in figure 4, low Nb alloys amplify 500 times of group under the conditions of 909 DEG C under the conditions of 895 DEG C
Knit as shown in Figure 5.From Fig. 3~5, middle temperature insulation, crystallite dimension in institutional framework are carried out under corresponding temperature conditionss
There is no bigger difference, and occur without mixed crystal, between 5%~10%, pattern should be corynebacterium to the content of δ phases after heating, it is long
The scope of ratio wide should be between 2~3, and this kind of state is optimal middle temperature holding temperature.
Embodiment 2
By three kinds of bars of difference Nb contents, bar specification is 220 × 360mm of Φ, and choosing core tissue carries out tissue sight
Examine.Different Nb contents, after carrying out the isothermal holding of 172min with the middle temperature holding temperature of identical, the guarantor for carrying out high-temperature heating
Temperature, chooses soak temperature in the range of 970~1070 DEG C, wherein the middle temperature temperature of Nb alloys high is 1012 DEG C and 1016
℃；The middle temperature temperature of middle Nb alloys is 1020 DEG C and 1012 DEG C, and the middle temperature temperature of low Nb alloys is 1030 DEG C and 1025 DEG C, insulation
Time is obtained by diameter of rod with the product of heat insulating coefficient 6min/10mm, is 132min.After completion soak, to not
Observed with the tissue result of sample, the tissue of Nb alloys high is as shown in fig. 6, middle Nb under the conditions of 1020 DEG C under the conditions of 1012 DEG C
The tissue of alloy is as shown in fig. 7, the tissue of low Nb alloys is as shown in figure 8, wherein Fig. 6~8 are respectively amplification under the conditions of 1030 DEG C
200 times of tissue topography's figure.From Fig. 6~8, soak is carried out under corresponding temperature conditionss, it is brilliant in institutional framework
Particle size does not have bigger difference, and occurs without mixed crystal, and the content of δ phases is less than 2% after heating, and pattern should be graininess, length and width
The scope of ratio should be between 1~1.2, and this kind of state is optimal soak temperature.
Embodiment 3
Nb alloys high are taken according to component shown in table 1, on the basis of embodiment 1 and embodiment 2, according to adding shown in Fig. 9
Thermal flow process figure heats to Nb alloys high.The institutional framework amplified after 200 times is as shown in Figure 10.
According to actual measurement gained：The equal temperature time for terminating integrally to reach target temperature to final bar is incubated from middle temperature is
70min, heating total time is 478min.
Embodiment 4
Middle Nb alloys are taken according to component shown in table 1, on the basis of embodiment 1 and embodiment 2, according to adding shown in Figure 11
Thermal flow process figure centering Nb alloys are heated.The institutional framework for amplifying 200 times is as shown in figure 12.
Embodiment 5
Low Nb alloys are taken according to component shown in table 1, on the basis of embodiment 1 and embodiment 2, according to adding shown in Figure 13
Thermal flow process figure heats to Nb alloys high.The institutional framework for amplifying 200 times is as shown in figure 14.
Tissue topography's figure that comparative example 1 and embodiment 3~5 are obtained is compared, comparison diagram 2, Figure 10 and Figure 14 understand,
According to the appearance for substantially having mixed crystal in the institutional framework that traditional heating mode is obtained, grain size is uneven, and according to the present invention
The institutional framework that obtains of technical scheme in crystallite dimension be more or less the same, occur without substantially huge crystal grain, it is known that, according to this hair
Be not in mixed crystal after bright mode of heating is heated to GH4169 alloys, and uniform texture.
Comparative example 1 and the Finite element analysis results of embodiment 3, it is known that, according to two-part mode of heating energy of the present invention
The same heating effect of Three-section type heating mode is enough realized, can cause that material integrally reaches height by middle temperature within the identical time
Temperature, but the overall heat time substantially reduce.
The above is only the preferred embodiment of the present invention, it is noted that for the ordinary skill people of the art
For member, under the premise without departing from the principles of the invention, some improvements and modifications can also be made, these improvements and modifications also should
It is considered as protection scope of the present invention.
Claims (8)
1. heating means before a kind of deformation of GH4169 alloys, it is characterised in that the first rank is carried out to the GH4169 alloys
Middle temperature insulation after Duan Jiare, carry out second stage heating to the alloy after the middle temperature insulation carries out soak again；In described
The temperature of temperature insulation is 880~920 DEG C, and the temperature of the soak is 1000~1045 DEG C.
2. heating means according to claim 1, it is characterised in that the heating rate of the first stage heating is 1.0
~3.0 DEG C/min；The heating rate of the second stage heating is 1.3~2.0 DEG C/min.
3. heating means according to claim 1, it is characterised in that according to the content setting of niobium in the GH4169 alloys
The temperature of the middle temperature insulation；
When niobium in the GH4169 alloys content for [4.75wt%, 5.0wt%) when, the temperature of the middle temperature insulation is [880
℃,895℃)；
When niobium in the GH4169 alloys content for [5.0wt%, 5.2wt%) when, the temperature of the middle temperature insulation is [895
℃,907℃)；
When the content of niobium in the GH4169 alloys is [5.2wt%, 5.5wt%], the temperature of the middle temperature insulation is [907
℃,920℃]。
4. heating means according to claim 1 or 3, it is characterised in that the temperature of the middle temperature insulation is according to following step
It is rapid to determine：
The temperature range of the middle temperature insulation of default GH4169 alloys, the temperature range of the default middle temperature insulation is 800~960
℃；
Isothermal holding is carried out to the GH4169 alloys within the scope of the default temperature；
Structure observation is carried out to GH4169 alloys after the isothermal holding；
According to the result of the structure observation, the temperature of the middle temperature insulation is obtained；
When the result of the structure observation meets middle temperature insulation organizational requirements, the temperature for obtaining the result is middle temperature insulation
Temperature；The middle temperature is incubated organizational requirements：There is no a mixed crystal, the percent by volume of δ phases is short for the pattern of 5%~10%, δ phases
Bar-shaped, the length-width ratio of δ phases is 2~3.
5. heating means according to claim 4, it is characterised in that within the temperature range of the default middle temperature insulation
Test temperature is chosen by gradient；The thermograde is 5~10 DEG C.
6. heating means according to claim 1, it is characterised in that niobium element in the GH4169 alloys contains
The temperature of the amount setting soak；
When niobium element in the GH4169 alloys content for [4.75wt%, 5.0wt%) when, the temperature of the soak is
[1000℃,1015℃)；
When niobium element in the GH4169 alloys content for [5.0wt%, 5.2wt%) when, the temperature of the soak is
[1015℃,1030℃)；
When the content of niobium in the GH4169 alloys is [5.2wt%, 5.5wt%], the temperature of the soak is [1030
℃,1045℃]。
7. heating means according to claim 1 or 6, it is characterised in that the temperature of the soak is according to following step
It is rapid to determine：
The temperature range of the soak of default GH4169 alloys, the temperature range of the default soak for 970~
1070℃；
Isothermal holding is carried out to the GH4169 alloys within the scope of the default temperature；
Structure observation is carried out to the GH4169 alloys after the isothermal holding；
According to the result of the structure observation, the temperature of the soak is obtained；
When the result of the structure observation meets soak organizational requirements, it is soak to obtain the temperature of the result
Temperature；The organizational requirements of the soak are：There is no a mixed crystal, the percent by volume of δ phases for 0~2%, δ phases pattern for
Granular, the length-width ratio of δ phases is 1~1.2.
8. heating means according to claim 7, it is characterised in that within the temperature range of the default soak
Test temperature is chosen by gradient；The thermograde is 5~10 DEG C.
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Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN107377841A (en) * | 2017-09-14 | 2017-11-24 | 上海怀德机电有限公司 | A kind of forging method of GH4169 alloys Ultra-fine Grained forging |
| CN110819922A (en) * | 2019-11-13 | 2020-02-21 | 中国航发动力股份有限公司 | Treatment method for improving GH4413G part organization |
| CN110885988A (en) * | 2019-12-16 | 2020-03-17 | 云南云铝海鑫铝业有限公司 | Natural gas roasting grooving method |
| CN111604448A (en) * | 2020-06-05 | 2020-09-01 | 重庆钢铁研究所有限公司 | Forging method of high-temperature alloy GH4099 |
| CN114540731A (en) * | 2022-02-23 | 2022-05-27 | 北京钢研高纳科技股份有限公司 | GH4169 alloy bar and preparation method and fastener thereof |
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| EP2138601A1 (en) * | 2008-06-16 | 2009-12-30 | Korea Institute Of Machinery & Materials | A heat treatment method of a ni-based superalloy for wave-type grain boundary and a ni-based superalloy produced accordingly |
| CN103831380A (en) * | 2013-12-15 | 2014-06-04 | 无锡透平叶片有限公司 | Die forging forming technology for GH4169 alloy forge piece |
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| EP2138601A1 (en) * | 2008-06-16 | 2009-12-30 | Korea Institute Of Machinery & Materials | A heat treatment method of a ni-based superalloy for wave-type grain boundary and a ni-based superalloy produced accordingly |
| CN103831380A (en) * | 2013-12-15 | 2014-06-04 | 无锡透平叶片有限公司 | Die forging forming technology for GH4169 alloy forge piece |
Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN107377841A (en) * | 2017-09-14 | 2017-11-24 | 上海怀德机电有限公司 | A kind of forging method of GH4169 alloys Ultra-fine Grained forging |
| CN110819922A (en) * | 2019-11-13 | 2020-02-21 | 中国航发动力股份有限公司 | Treatment method for improving GH4413G part organization |
| CN110885988A (en) * | 2019-12-16 | 2020-03-17 | 云南云铝海鑫铝业有限公司 | Natural gas roasting grooving method |
| CN111604448A (en) * | 2020-06-05 | 2020-09-01 | 重庆钢铁研究所有限公司 | Forging method of high-temperature alloy GH4099 |
| CN114540731A (en) * | 2022-02-23 | 2022-05-27 | 北京钢研高纳科技股份有限公司 | GH4169 alloy bar and preparation method and fastener thereof |
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