CN106756683B - 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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- CN106756683B CN106756683B CN201611096345.7A CN201611096345A CN106756683B CN 106756683 B CN106756683 B CN 106756683B CN 201611096345 A CN201611096345 A CN 201611096345A CN 106756683 B CN106756683 B CN 106756683B
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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
Abstract
The present invention provides heating means before a kind of deformation of GH4169 alloys, and medium temperature is kept the temperature after carrying out first stage heating to the GH4169 alloys, and the alloy after being kept the temperature to the medium temperature carries out second stage heating and carries out soak again；The temperature of the medium temperature heat preservation is 880~920 DEG C, and the temperature of the soak is 1000~1045 DEG C.Method provided by the invention heats GH4169 alloys using two-part, and compared with prior art, heating time is only the 2/3 of conventional Three-section type heating time, and the efficiency of heating surface improves；The heating temperature kept the temperature using 880~920 DEG C as medium temperature is avoided that overlapping for peak temperature is precipitated with δ phases, realizes the control to δ phase morphologies, improves structural homogenity.
Description
Technical field
The present invention relates to heating sides before GH4169 Alloy Processings field more particularly to a kind of deformation of GH4169 alloys
Method.
Background technology
High temperature alloy is the high alloy for referring to bear larger complex stress at 600 DEG C or more, and having 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 higher high temperature alloys of alloying level, are the high temperature alloys being most widely used.But
It is that GH4169 alloy hot performances are poor, needs to heat it before GH4169 alloy machining deformations, ensures
GH4169 alloys have good plasticity in deformation after unloading process, 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 manufacturing method, specifically discloses using at three sections of mode of heatings
Blank is managed, blank is heated in a manner of 845~855 DEG C, 980~990 DEG C, 1015~1025 DEG C of three sections of heating；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, become to be follow-up
Shape processing provides stabilizing tissue.But in existing Three-section type heating specification, medium temperature holding temperature is mostly between 940~985 DEG C,
The peak temperature that this temperature is precipitated close to δ phases keeps the temperature, inevitably results in δ phase morphologies and distribution does not conform at this temperature for a long time
It is suitable, cause the component segregation of microcell in alloy, causes forging performance inhomogenous.It can be seen that formulating heating rule before rational forging
Important link when model under forging technology.
Invention content
In view of this, the purpose of the present invention is to provide heating means before a kind of deformation of GH4169 alloys, can improve
Obtain the structural homogenity of alloy product.
In order to achieve the above-mentioned object of the invention, the present invention provides following technical scheme：
Heating means before a kind of deformation of GH4169 alloys, which is characterized in that first is carried out to the GH4169 alloys
Medium temperature is kept the temperature after stepwise heating, and the alloy after being kept the temperature to the medium temperature carries out second stage heating and carries out soak again；It is described
The temperature of medium temperature heat preservation 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 of the medium temperature heat preservation is set according to the content of niobium element in the GH4169 alloys；
When the content of niobium element in the GH4169 alloys is [4.75wt%, 5.0wt%) when, the temperature of medium temperature heat preservation
Degree for [880 DEG C, 895 DEG C)；
When the content of niobium element in the GH4169 alloys is [5.0wt%, 5.2wt%) when, the temperature of medium temperature heat preservation
Degree 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 medium temperature heat preservation
Degree is [907 DEG C, 920 DEG C].
Preferably, the temperature of the medium temperature heat preservation determines according to the following steps：
The temperature range of the temperature range of the medium temperature heat preservation of default GH4169 alloys, the preset medium temperature heat preservation 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 structure observation as a result, obtaining the temperature of the medium temperature heat preservation；
When the result of the structure observation, which meets medium temperature, keeps the temperature organizational requirements, obtains the temperature of the result and protected for medium temperature
The temperature of temperature；The medium temperature keeps the temperature organizational requirements：It is the pattern of 5%~10%, δ phases not have mixed crystal, the percent by volume of δ phases
Length-width ratio for corynebacterium, δ phases is 2~3.
Preferably, within the temperature range of the preset medium temperature heat preservation temperature to be tested is chosen by gradient；The temperature
Gradient is 5~10 DEG C.
Preferably, the temperature of the soak is set according to the content of the niobium element in the GH4169 alloys；
When niobium element in the GH4169 alloys content be [4.75wt%, 5.0wt%) when, the temperature of the soak
Degree for [1000 DEG C, 1015 DEG C)；
When niobium element in the GH4169 alloys content be [5.0wt%, 5.2wt%) when, the temperature of the soak
Degree 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
Degree is [1030 DEG C, 1045 DEG C].
Preferably, the temperature of the soak determines according to the following steps：
The temperature range of the temperature range of the soak of default GH4169 alloys, the preset 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 structure observation as a result, obtaining the temperature of the soak；
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 percents by volume of δ phases is that the pattern of 0~2%, δ phases is
The length-width ratio of graininess, δ phases is 1~1.2.
Preferably, within the temperature range of the preset soak test temperature is chosen by gradient；The temperature ladder
Degree is 5~10 DEG C.
The present invention provides heating means before a kind of deformation of GH4169 alloys, and the first rank is carried out to the GH4169 alloys
Medium temperature is kept the temperature after Duan Jiare, and the alloy after being kept the temperature to the medium temperature carries out second stage heating and carries out soak again；In described
The temperature of temperature heat preservation is 880~920 DEG C, and the temperature of the soak is 1000~1045 DEG C.Method provided by the invention is right
GH4169 alloys are heated using two-part, and compared with prior art, heating time is only the 2/3 of conventional Three-section type heating time,
The efficiency of heating surface improves；The heating temperature kept the temperature using 880~920 DEG C as medium temperature is avoided using the weight that peak temperature is precipitated with δ phases
It closes, realizes the control to the form of δ phases, improve structural homogenity.Embodiment the result shows that, using two-part mode of heating energy
Enough reach the identical equal temperature time with Three-section type heating mode, it is seen that under the premise of the shortening heating time raising efficiency of heating surface still
It can ensure that heating effect；Technical solution using the present invention heats GH4169 alloys, obtains in tissue without mixed
Brilliant appearance, and grain boundaries precipitated phase is few, and precipitated phase length-width ratio controls in 1~1.2 range, uniform texture.
Further, the temperature and high temperature of different medium temperature heat preservations are limited according to the different niobium element contents of GH4169 alloys
Holding temperature avoids, using the mode of heating lumped together, fully considering niobium element content to the second precipitated phase δ in heating process
The content of phase and the influence of pattern obtain suitable δ phases content and δ phase morphology features, while it is big to avoid Grain-Boundary Phase from being precipitated
The segregation of niobium element caused by the δ phases of amount, and then control structural homogenity.
Description of the drawings
The present invention will be further described in detail below with reference to the accompanying drawings and specific embodiments.
Fig. 1 is the heating procedure figure of comparative example 1 of the present invention；
Fig. 2 is the alloy structure shape appearance figure that comparative example 1 of the present invention obtains；
Tissue topography after Fig. 3 keeps the temperature for high Nb alloys in the embodiment of the present invention 1 under the conditions of 890 DEG C schemes；
Fig. 4 is tissue topography's figure after the middle Nb alloys of the embodiment of the present invention 1 are kept the temperature under the conditions of 895 DEG C；
Fig. 5 is tissue topography's figure after the low Nb alloys in the embodiment of the present invention 1 are kept the temperature under the conditions of 909 DEG C；
Tissue topography after Fig. 6 keeps the temperature for high Nb alloys in the embodiment of the present invention 2 under the conditions of 1012 DEG C schemes；
Fig. 7 is tissue topography's figure after the middle Nb alloys in the embodiment of the present invention 2 are kept the temperature under the conditions of 1020 DEG C；
Fig. 8 is tissue topography's figure after the low Nb alloys in the embodiment of the present invention 2 are kept the temperature under the conditions of 1030 DEG C；
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 obtains；
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 obtains；
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 obtains.
Specific implementation mode
The present invention provides the heating means before a kind of deformation of GH4169 alloys, and first is carried out to the GH4169 alloys
Medium temperature is kept the temperature after stepwise heating, and the alloy after being kept the temperature to the medium temperature carries out second stage heating and carries out soak again；It is described
The temperature of medium temperature heat preservation is 880~920 DEG C, and the temperature of the soak is 1000~1045 DEG C.
Method provided by the invention, it is only three sections conventional to use two-part mode of heating, heating time to GH4169 alloys
The 2/3 of formula heating time, the efficiency of heating surface improve；The heating temperature kept the temperature using 880~920 DEG C as medium temperature avoids using and δ phases
The coincidence of peak temperature is precipitated, realizes the control to the form of δ phases, improves structural homogenity.
The GH4169 alloys are carried out medium temperature heat preservation by the present invention first, and the temperature of the medium temperature heat preservation 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 rodlike or plank.The present invention does not have particular/special requirement to the source of the GH4169 alloys, using art technology
GH4169 alloys known to personnel.
The present invention is in order to determine the temperature of the medium temperature heat preservation, and preferably first the medium temperature of default GH4169 alloys is kept the temperature the present invention
Temperature range, ranging from 800~960 DEG C of the preset medium temperature holding temperature；
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 structure observation as a result, obtaining the temperature of the medium temperature heat preservation；
When the result of the structure observation, which meets medium temperature heat preservation, to be organized as requiring, the temperature for obtaining the result is medium temperature
The temperature of heat preservation；The organizational requirements of medium temperature heat preservation 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 preset medium temperature heat preservation is preferably 800~960 DEG C.In the present invention, institute
The temperature range for stating medium temperature heat preservation is preferably the temperature range of the medium temperature heat preservation of conventional Three-section type heating mode.
After the temperature range of the medium temperature heat preservation of default GH4169 alloys, the present invention is within the scope of the default temperature to institute
It states GH4169 alloys and carries out isothermal holding.In order to preferably filter out effect preferably temperature, the present invention is preferably described default
Medium temperature heat preservation within the temperature range of take different temperature.The present invention preferably presses gradient and chooses test temperature in the temperature range
Degree；In the present invention, the temperature gradient is preferably 5~10 DEG C, further preferably 6~9 DEG C, more preferably 7~8 DEG C.This
Invention is preferably multiplying by the size of heating alloy and soaking time coefficient in the time of the preset temperature range inside holding
Product；In the present invention, the heat insulating coefficient of the medium temperature heat preservation is preferably 8min/10mm.In the present invention, the medium temperature was kept the temperature
The alloy of journey is GH4169 alloy raw materials, and size is preferably determined with the shape of the GH4169 alloys：When the GH4169 is closed
When gold is plank, the size by heating alloy is the thickness of the plank；It is described when the GH4169 alloys are bar
By the diameter that the size of heating alloy is the bar；It is described to be closed by heating when the GH4169 alloys are irregular shape
The size of gold is the size in the most thick direction of the irregular shape.
To the GH4169 alloys under the conditions of different test temperatures after isothermal holding, the present invention preferably to the heat preservation at
GH4169 alloys after reason carry out structure observation after carrying out cooling.In the present invention, the temperature after cooling is preferably room temperature,
Further 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 are specially water cooling.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 the embodiment of the present invention
In, structure observation is specifically carried out to the GH4169 alloys using light microscope.
After completing the structure observation, the present invention according to observed as a result, set to the GH4169 alloys carry out in
The temperature of temperature heat preservation.Specifically, in the present invention, it, will when the result of the structure observation, which meets medium temperature, keeps the temperature organizational standard
Corresponding isothermal holding temperature is set as the temperature of medium temperature heat preservation.In the present invention, the organizational requirements of the medium temperature heat preservation are preferred
For：There is no a mixed crystal, the percents by volume of δ phases is that the pattern of 5%~10%, δ phases is corynebacterium, and the length-width ratio of δ phases is 2~3.This
In the organizational requirements for inventing the medium temperature heat preservation, the percent by volume of the δ phases is more preferably 6%~9%, more preferably
7%~8%；In the organizational requirements of medium temperature heat preservation 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 medium temperature defined by is kept the temperature, in different test temperature
Medium temperature isothermal holding is carried out to the GH4169 alloys under the conditions of degree, is determined according to organizational standard combination structure observation result optimal
Medium temperature heat preservation temperature, realize the control to Second Phase Precipitation in heating process.
In the present invention, the temperature of the medium temperature heat preservation is 880~920 DEG C.The present invention is preferably closed according to the GH4169
The content of niobium element sets the temperature of the medium temperature heat preservation in gold：
When the content of niobium element in the GH4169 alloys is [4.75wt%, 5.0wt%) when, the temperature of medium temperature heat preservation
Degree be preferably [880 DEG C, 895 DEG C), further preferably 885 DEG C~890 DEG C；
When the content of niobium element in the GH4169 alloys is [5.0wt%, 5.2wt%) when, the temperature of medium temperature heat preservation
Degree be preferably [895 DEG C, 907 DEG C), further 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 medium temperature heat preservation
It spends preferably [907 DEG C, 920 DEG C], further preferably 910 DEG C~915 DEG C.
The present invention limits the GH4169 alloys of different niobium element contents the temperature of different medium temperature heat preservations, avoids using one
Mode of heating in general fully considers niobium element content to the content of the second precipitated phase δ phases in heating process and pattern
It influences, obtains suitable δ phases content and δ phase morphology features, while avoiding the niobium member caused by a large amount of δ phases of Grain-Boundary Phase precipitation
The segregation of element, and then control structural homogenity.
In the present invention, the first stage heating preferably is selected from 750 DEG C and heats up, and reaches the temperature of the medium temperature heat preservation
Degree.In the present invention, the heating rate of the first stage heating is preferably 1.0~3.0 DEG C/min, further preferably 1.2
~2.7 DEG C/min, more preferably 1.5~2.2 DEG C/min.The present invention does not have special want to the control mode of the heating rate
It asks, using the control mode of heating rate well-known to those skilled in the art；The embodiment of the present invention, which specifically uses, to be added
The 80~90% of thermal instrument general power are heated, and further preferably 86~88%.The present invention is to the heating instrument total work
Rate does not have particular/special requirement, and GH4169 alloys heating instrument general power is used for using well-known to those skilled in the art.
In the present invention, under the ramp rate conditions, when successfully avoiding that the rate of heat addition is too fast in traditional heating mode,
Forging internal temperature field is uneven, it is possible that the defects of filling is discontented, crackle during deformation after unloading after the completion of heating；Together
Sample avoids that the rate of heat addition is excessively slow, leads to coarse-grain occur inside the blank after heating, once the deflection in deformation process is insufficient
In so that coarse-grain perfect recrystallization, the tissue of the deformation of final molding is there is defect, quality will be affected the problem of.
In the present invention, the soaking time of the medium temperature holding stage is preferably by the size and soaking time of heating alloy
The product of coefficient；In the present invention, the heat insulating coefficient of the medium temperature heat preservation is preferably 8min/10mm.In the present invention, in described
Warm holding stage is GH4169 alloy raw materials by heating alloy, and size is preferably determined with the shape of the GH4169 alloys：
When the GH4169 alloys are plank, the size by heating alloy is the thickness of the plank；When the GH4169 is closed
When gold is bar, the size by heating alloy is the diameter of the bar；When the GH4169 alloys are irregular shape
When, the size by heating alloy is the size in the most thick direction of the irregular shape.
For the present invention in order to determine the temperature of the soak, the present invention preferably first presets the soak of GH4169 alloys
Temperature range, the preset 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 structure observation as a result, obtaining the temperature of the soak；
When the result of the structure observation, which meets soak organizational standard, to be required, the temperature for obtaining the result is height
The temperature of temperature heat preservation；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 preset 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
It states GH4169 alloys and carries out isothermal holding.In order to preferably filter out effect preferably temperature, the present invention is preferably in the height of acquisition
Different temperature is taken within the scope of warm holding temperature.The present invention preferably presses gradient and chooses test temperature in the temperature range；
In the present invention, the temperature gradient is preferably 5~10 DEG C, further preferably 6~9 DEG C, more preferably 7~8 DEG C.The present invention exists
The time kept the temperature within the temperature range of the acquisition is preferably by the product of the size of heating alloy and 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 medium temperature holding stage
Heating alloy is GH4169 alloy raw materials, and size is preferably determined with the shape of the GH4169 alloys：When the GH4169 is closed
When gold is plank, the size by heating alloy is the thickness of the plank；It is described when the GH4169 alloys are bar
By the diameter that the size of heating alloy is the bar；It is described to be closed by heating when the GH4169 alloys are irregular shape
The size of gold is the size in the most thick direction of the irregular shape.
To the GH4169 alloys under the conditions of different test temperatures after isothermal holding, the present invention preferably to the heat preservation at
GH4169 alloys after reason carry out structure observation after carrying out cooling.The present invention to the type of cooling preferably as described above
Scheme carries out, and details are not described herein.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, specifically using light microscope to the GH4169
Alloy carries out structure observation.
After completing the structure observation, the present invention according to it is obtained observation as a result, setting to the GH4169 alloys into
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 to the temperature of soaking period.In the present invention, the soak tissue is wanted
It asks preferably：There is no a mixed crystal, the percents by volume of δ phases is that the pattern of 0~2%, δ phases is graininess shape, and the length-width ratio of δ phases is 1
~1.2.In soak organizational requirements of the present invention, the percents 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 defined by within the temperature range of soak, 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 combination structure 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
Degree is 1000~1045 DEG C.
The present invention preferably sets the temperature of the soak according to the content of niobium element in the GH4169 alloys：Work as institute
State niobium element in GH4169 alloys content be [4.75wt%, 5.0wt%) when, the temperature of the soak is preferably
[1000 DEG C, 1015 DEG C), further 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 be [5.0wt%, 5.2wt%) when, the temperature of the soak is preferably [1015
DEG C, 1030 DEG C), further preferably 1020 DEG C~1028 DEG C, most preferably 1025 DEG C；When niobium element in the GH4169 alloys
Content when being [5.2wt%, 5.5wt%], the temperature of the soak is preferably [1030 DEG C, 1045 DEG C], further excellent
1032 DEG C~1042 DEG C are selected as, more preferably 1035 DEG C~1040 DEG C, most preferably 1038 DEG C.The present invention contains different niobium elements
The GH4169 alloys of amount limit the temperature of different soaks, avoid, using the mode of heating lumped together, fully considering niobium
Influence of the constituent content to the content of the second precipitated phase δ phases and pattern in heating process, obtains suitable δ phases content and δ phases
Shape characteristic, while the segregation of the niobium element caused by a large amount of δ phases of Grain-Boundary Phase precipitation is avoided, and then control even tissue
Property.
Alloy progress second stage heating after the present invention keeps the temperature the medium temperature carries out soak again；In the present invention
In, the temperature that the second stage heating preferably is selected from the medium temperature heat preservation heats up, and reaches the temperature of the soak.
In the present invention, the time interval of the first stage heating and medium temperature insulating process and second stage heating and soak process
It is 0, i.e., carries out medium temperature heat preservation after the described first stage heating, second stage heating is directly carried out after completing the medium temperature heat preservation.
In the present invention, the first stage heats and medium temperature insulating process is heated with second stage and soak process is preferably in phase
It is 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
For 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；The embodiment of the present invention is specifically adopted
It is heated with the 75~85% of heating instrument general power, further preferably 78~80%.The present invention is to the heating instrument
General power does not have particular/special requirement, is with instrument general power for the heating of GH4169 alloys using well-known to those skilled in the art
It can.
In the present invention, the restriction of the heating rate of the second stage heating equally successfully avoids 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 of discontented, crackle；It avoids that the rate of heat addition is excessively slow simultaneously, leads to coarse-grain occur inside the blank after heating, once deformation
Deflection in the process is not enough to that coarse-grain perfect recrystallization, the tissue of the deformation of final molding is made to there is defect, and quality will
The problem of being affected.
In the present invention, the soaking time of the soak is preferably by the size of heating alloy and soaking time coefficient
Product；In the present invention, the heat insulating coefficient of the soak is preferably 6min/10mm.In the present invention, the high temperature dwell
Thermophase is GH4169 alloy raw materials by heating alloy, and size is preferably determined with the shape of the GH4169 alloys：Work as institute
State GH4169 alloys be plank when, the size by heating alloy be the plank thickness；When the GH4169 alloys are
When bar, the size by heating alloy is the diameter of the bar；When the GH4169 alloys are irregular shape, institute
It states by the size in the most thick direction that the size of heating alloy is the irregular shape.
The present invention keeps the temperature the medium temperature and the mode of heating of soak does not have particular/special requirement, using people in the art
Mode of heating known to member.In an embodiment of the present invention, specific to be carried out in such a way that heat treatment is heated.In this hair
In bright, the interlude of the medium temperature heating and high-temperature heating is preferably 0~5min, further preferably 0.5~2min.
The present invention provides the heating means before a kind of deformation of GH4169 alloys, and first is carried out to the GH4169 alloys
Medium temperature is kept the temperature after stepwise heating, and the alloy after being kept the temperature to the medium temperature carries out second stage heating and carries out soak again；It is described
The temperature of medium temperature heat preservation is 880~920 DEG C, and the temperature of the soak is 1000~1045 DEG C.Method provided by the invention,
It is only the 2/3 of conventional Three-section type heating time to use two-part mode of heating, heating time to GH4169 alloys, and the efficiency of heating surface carries
It is high；The heating temperature kept the temperature using 880~920 DEG C as medium temperature is avoided that overlapping for peak temperature is precipitated using with δ phases, realized to δ
The control of the form of phase improves structural homogenity.
The heating means before the deformation of GH4169 alloys provided by the invention are carried out specifically with reference to embodiment
It is bright, but they cannot be interpreted as limiting the scope of the present invention.
It is divided into high Nb alloys (4.75~5.0%) according to Nb contents in GH4169 alloys, middle Nb alloys (5.0~
And low Nb alloys (5.2~5.5%) 5.2%).Component alloy described in table 1 is heated.
1 three kinds of GH4169 alloy compositions of table
Comparative example 1
High niobium alloy A, middle niobium alloy B and low niobium alloy C are taken, according to flow chart shown in FIG. 1, these three alloys are carried out
Three-section type heating processing, and Observation of Histological Structure is carried out to the alloy after heating, observation result is as shown in Fig. 2, and wherein a is height
The tissue topography of niobium alloy A schemes, and b is that the tissue topography of middle niobium alloy schemes, and c is that the tissue topography of low niobium alloy schemes, and is amplification
200 times of tissue topography's figures.And it is simulated using finite element software, it can be deduced that：Terminate from medium temperature heat preservation to final
Bar integrally reach a high temperature heating target temperature equal temperature time be 70min, heating total time be 548min.Wherein high Nb is closed
Tissue topography's figure of gold occur crystallite dimension differ greatly, mixed crystal size it is big, the case where range wide serious nonuniform organization.
Locally there is strip big crystal grain in the tissue topography of middle Nb alloys, and rest part 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, and 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 the bar of three kinds of difference Nb contents, bar specification is 220 × 360mm of Φ, chooses core tissue and carries out tissue sight
It examines.Different Nb contents choose medium temperature holding temperature, wherein the medium temperature temperature of high Nb alloys is within the scope of 800~960 DEG C
850 DEG C and 890 DEG C；The medium temperature temperature of middle Nb alloys is 895 DEG C and 890 DEG C, and the medium temperature temperature of low Nb alloys is 909 DEG C and 900
DEG C, soaking time is obtained by diameter of rod and the product of heat insulating coefficient 8min/10mm, is 176min.It completes medium temperature and keeps the temperature it
Afterwards, the tissue result of various sample is observed, under the conditions of 890 DEG C high Nb alloys 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
It knits as shown in Figure 5.By Fig. 3~5 it is found that carrying out medium temperature heat preservation under corresponding temperature condition, crystallite dimension in institutional framework
There is no bigger difference, and mixed crystal do not occur, for the content of δ phases between 5%~10%, pattern should be corynebacterium after heating, long
The range of wide ratio should be between 2~3, and such state is best medium temperature holding temperature.
Embodiment 2
By the bar of three kinds of difference Nb contents, bar specification is 220 × 360mm of Φ, chooses core tissue and carries out tissue sight
It examines.Different Nb contents, after the isothermal holding that 172min is carried out with identical medium temperature holding temperature, the guarantor that is heated at high temperature
Temperature chooses soak temperature within the scope of 970~1070 DEG C, wherein the medium temperature temperature of high Nb alloys is 1012 DEG C and 1016
℃；The medium temperature temperature of middle Nb alloys is 1020 DEG C and 1012 DEG C, and the medium temperature temperature of low Nb alloys is 1030 DEG C and 1025 DEG C, heat preservation
Time is obtained by diameter of rod and the product of heat insulating coefficient 6min/10mm, is 132min.After completing soak, to not
Tissue result with sample is observed, and the tissue of high Nb alloys 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 to amplify under the conditions of 1030 DEG C
200 times of tissue topography's figure.It is brilliant in institutional framework by Fig. 6~8 it is found that carrying out soak under corresponding temperature condition
Particle size does not have bigger difference, and mixed crystal does not occur, and the content of δ phases is less than 2% after heating, and pattern should be graininess, length and width
The range of ratio should be between 1~1.2, and such state is best soak temperature.
Embodiment 3
High Nb alloys are taken according to component shown in table 1, on the basis of embodiment 1 and embodiment 2, are added according to shown in Fig. 9
Thermal flow process figure heats high Nb alloys.Institutional framework after 200 times of amplification is as shown in Figure 10.
According to actual measurement gained：The equal temperature time for terminating to final bar integrally to reach target temperature is kept the temperature from medium temperature is
70min, heating total time are 478min.
Embodiment 4
Middle Nb alloys are taken according to component shown in table 1, on the basis of embodiment 1 and embodiment 2, are added according to shown in Figure 11
Thermal flow process figure centering Nb alloys are heated.The institutional framework of 200 times of amplification 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, are added according to shown in Figure 13
Thermal flow process figure heats high Nb alloys.The institutional framework of 200 times of amplification is as shown in figure 14.
Tissue topography's figure that comparative example 1 and embodiment 3~5 obtain is compared, comparison diagram 2, Figure 10 and Figure 14 it is found that
Obviously there is the appearance of mixed crystal in the institutional framework obtained according to traditional heating mode, grain size is uneven, and according to the present invention
The obtained institutional framework of technical solution in crystallite dimension be not much different, occur without apparent huge crystal grain, it is known that, according to this hair
It is not in mixed crystal after bright mode of heating heats GH4169 alloys, and uniform texture.
The Finite element analysis results of comparative example 1 and embodiment 3, it is known that, according to two-part mode of heating energy of the present invention
Enough realize the same heating effect of Three-section type heating mode, it can be interior at the same time so that material is whole to reach high by medium temperature
Temperature, but overall heating time be substantially reduced.
The above is only a preferred embodiment of the present invention, it is noted that for the ordinary skill people of the art
For member, various improvements and modifications may be made without departing from the principle of the present invention, these improvements and modifications are also answered
It is considered as protection scope of the present invention.
Claims (7)
1. the heating means before a kind of deformation of GH4169 alloys, which is characterized in that carry out the first rank to the GH4169 alloys
Medium temperature is kept the temperature after Duan Jiare, and the alloy after being kept the temperature to the medium temperature carries out second stage heating and carries out soak again；In described
The temperature of temperature heat preservation is 880~920 DEG C, and the temperature of the soak is 1000~1045 DEG C；
The temperature of the medium temperature heat preservation is set according to the content of niobium in the GH4169 alloys；
When the content of niobium in the GH4169 alloys is [4.75wt%, 5.0wt%) when, the temperature of medium temperature heat preservation is [880
℃,895℃)；
When the content of niobium in the GH4169 alloys is [5.0wt%, 5.2wt%) when, the temperature of medium temperature heat preservation is [895
℃,907℃)；
When the content of niobium in the GH4169 alloys is [5.2wt%, 5.5wt%], the temperature of the medium temperature heat preservation is [907
℃,920℃]。
2. heating means according to claim 1, which is characterized 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, which is characterized in that the temperature of the medium temperature heat preservation is true according to the following steps
It is fixed：
The temperature range of the temperature range of the medium temperature heat preservation of default GH4169 alloys, the preset medium temperature heat preservation 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 structure observation as a result, obtaining the temperature of the medium temperature heat preservation；
When the result of the structure observation, which meets medium temperature, keeps the temperature organizational requirements, the temperature for obtaining the result is medium temperature heat preservation
Temperature；The medium temperature keeps the temperature organizational requirements：There is no mixed crystal, it is short that the percent by volume of δ phases, which is the pattern of 5%~10%, δ phases,
Rodlike, the length-width ratio of δ phases is 2~3.
4. heating means according to claim 3, which is characterized in that within the temperature range of the preset medium temperature heat preservation
Test temperature is chosen by gradient；The temperature gradient is 5~10 DEG C.
5. heating means according to claim 1, which is characterized in that according to containing for the niobium element in the GH4169 alloys
Amount sets the temperature of the soak；
When niobium element in the GH4169 alloys content be [4.75wt%, 5.0wt%) when, the temperature of the soak is
[1000℃,1015℃)；
When niobium element in the GH4169 alloys content be [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℃]。
6. heating means according to claim 1 or 5, which is characterized 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 preset soak is 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 structure observation as a result, obtaining the temperature of the soak；
When the result of the structure observation meets soak organizational requirements, the temperature for obtaining the result is soak
Temperature；The organizational requirements of the soak are：There is no a mixed crystal, the percents by volume of δ phases is that the pattern of 0~2%, δ phases is
Granular, the length-width ratio of δ phases is 1~1.2.
7. heating means according to claim 6, which is characterized in that within the temperature range of the preset soak
Test temperature is chosen by gradient；The temperature gradient is 5~10 DEG C.
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| CN110819922B (en) * | 2019-11-13 | 2021-07-27 | 中国航发动力股份有限公司 | Treatment method for improving GH4413G part organization |
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| CN114540731B (en) * | 2022-02-23 | 2022-09-20 | 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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| Publication number | Priority date | Publication date | Assignee | Title |
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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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