CN107976462A - A kind of method for optimizing aluminum alloy heat processing technology - Google Patents
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Abstract
The present invention provides a kind of method for optimizing aluminum alloy heat processing technology, it is the hot rheology characteristic in thermal deformation process according to aluminium alloy, builds the hot working chart of alloy.The optimum thermal process parameter of alloy is determined by considering the size of place of safety and instability area in manuscript, dynamic recrystallization generating region, equivalent contour line rarefaction and power consumption values, so as to effectively control the microstructure of alloy, its hot-working character is improved.This method formulates hot-working system using the stability of dynamic recrystallization behavior and deformation mechanism of the aluminium alloy in thermal deformation process, and applicability is wide, it is easy to accomplish industrial-scale production, suitable for each line aluminium alloy material.Step is simple, considers comprehensively, highly practical.
Description
Technical field
The invention belongs to aluminium alloy manufacture field, is specifically designed a kind of method for optimizing aluminum alloy heat processing technology.
Background technology
Aluminium alloy has the excellent synthesis such as high specific stiffness and specific strength, good corrosion resistance and higher toughness
Mechanical property.Meanwhile it can be processed to extrusion or thin thick plate etc., therefore also possesses good processing performance.Therefore, aluminium closes
Gold is commonly utilized in the important feature component such as fuselage skin, bulkhead and wing, is the most important structure of aerospace industry
One of material.
Since plasticity of the aluminium alloy in room temperature is relatively low, crystallized ability is poor, and the heat processing technique of aluminium alloy (is such as extruded, rolled
System and forging etc.) have been widely used for producing all kinds of important aircraft structural parts.The selection pairing of thermal process parameter
The microstructure or mechanical performance important of gold.If thermal process parameter selection is improper, the rheologies such as crackle are easily led to
Unstability feature produces, and directly results in workpiece calcellation.
The hot working chart built according to dynamic material model (DMM) is the important tool for optimizing thermal process parameter.
At present, existing many scholars study hot working chart for alloy heat processing technique, become evaluation alloy hot-workability and optimization
The main method of heat processing technique.Patent of invention《A kind of magnesium alloy heat processing technique New Optimizing Method》(application number：
CN201710028472.1 proposed in) after being overlapped the DMM hot working charts of alloy and dynamic recrystallization contour map, selection
The hot-working suitable as alloy with the deformation parameter corresponding to the common region of the complete dynamic recrystallization of generation of process safety area
Technological parameter.The method exports the dynamic recrystallization volume fraction of magnesium alloy in a manner of contour map, can accurately control magnesium
Dynamic recrystallization behavior of the alloy in thermal deformation process.But the method is in the thermal process parameter of optimized alloy, not
Consider the influence of DMM manuscript medium value profile line density pairing gold deformation mechanisms, there is certain limitation.Equivalent contour line
Density there is material impact to the deformation mechanism of alloy because when alloy deforms in the densely distributed region of equivalent contour line
When, deformation mechanism is highly prone to the influence of deformation parameter, and plastic history is unstable, is unfavorable for processing.On the contrary, alloy is waiting
Thermal deformation can produce the rheological behaviour of stable state under conditions of value contour line is sparse.Therefore it provides a kind of heat for aluminium alloy
Processing technology optimization method is of great significance.
The content of the invention
In order to overcome above-mentioned deficiency, the present invention provides a kind of method for optimizing aluminum alloy heat processing technology, and the method is abundant
Consider influence of the hot working chart medium value profile line density to deformation mechanism.This method was both used by power dissipation figure and unstability
The hot working chart that figure is formed by stacking avoids material from producing manufacturing deficiency in hot procedure, and combines dynamic recrystallization
Area, equivalent contour line rarefaction and power consumption values size determine the optimum thermal process parameter of alloy, can produce
The rheological behaviour of stable state.
To achieve these goals, the present invention adopts the following technical scheme that：
A kind of method for optimizing aluminum alloy heat processing technology, including：
(1) aluminum alloy specimen is subjected to thermal modeling test, obtains thermal simulation experiment data；
(2) according to the thermal simulation experiment data, hot working chart is drawn by interpolation and the method for matrixing；
(3) true stress-true strain curve is drawn according to the thermal simulation experiment data, passes through work hardening rate processing method
Determine that the condition of dynamic recrystallization occurs for alloy, and dynamic recrystallization generation area is drawn in hot working chart；
(4) in place of safety with marking that power consumption values are higher and equivalent contour line is sparse in the lap of dynamic recrystallization generating region
Region, the deformation condition corresponding to this region is the optimum thermal process parameter of alloy.
(5) according to corresponding to the equivalent contour line is sparse, power consumption values are higher and the safety zone of dynamic recrystallization occurs
Deformation Parameters aluminum alloy materials are processed, to obtain the final product.
Preferably, the aluminum alloy specimen is Al-Zn-Mg-Cu systems alloy.
In order to match with hot modeling test machine, currently preferred aluminum alloy specimen size is 10 × 15mm of Φ.
Preferably, in the thermal simulation experiment, deformation temperature is 350-450 DEG C, strain rate 0.001-1s-1。
Preferably, the hot working chart is superimposed by the power dissipation figure and unstability figure obtained by thermal simulation experiment data
Obtain together.
Preferably, the work hardening rate processing method is：On the basis of true stress-true strain curve, draw successively
Go out ln θ-ε figure andCurve map, wherein θ refer to work hardening rate andε refers to strain.If ln θ-ε scheme
There are flex point orThere are minimum point (minimum value), then alloy dynamically to be tied again under this deformation condition for figure
Crystalline substance, and the corresponding strain of minimum point is the critical strain of dynamic recrystallization；If ln θ-ε figures there is no flex point or
Without minimum point or minimum value, then alloy dynamic recrystallization does not occur for figure.
Preferably, the step of thermal simulation experiment is：Thermocouple is first passed through by sample with the heating speed of (2-10) DEG C/s
Rate is heated to preset temperature, keeps the temperature and carries out uniform speed's isothermal hot compression test according to experimental program after (3-5) min.Work as deflection
Stop compression after reaching (50-60) %, sample is quenched rapidly into the water.
Present invention also offers a kind of aluminium alloy processing method, including：
Aluminum alloy specimen is analyzed according to any above-mentioned method, acquisition includes place of safety and unstability accordingly
Area, dynamic recrystallization generating region, the hot working chart of equivalent contour line rarefaction；
According to above-mentioned hot working chart, the equivalent contour line of selection is sparse, power consumption values are higher and the peace of dynamic recrystallization occurs
Region-wide corresponding Deformation Parameters are processed aluminum alloy materials, to obtain the final product.
Beneficial effects of the present invention：
(1) present invention has taken into full account influence of the dynamic recrystallization to alloy hot deformation behavior.At work hardening rate
Reason method, determines that the condition of dynamic recrystallization occurs for alloy, and dynamic recrystallization generation area is drawn in hot working chart；
(2) present invention has taken into full account the influence of power consumption values size and equivalent profile line density pairing gold thermal deformation process.
The equivalent contour line of selection is sparse in hot working chart, power consumption values are higher and the safety zone of dynamic recrystallization occurs to alloy material
It is processed, can have not only ensured that Rheological Instability does not occur for material, but also can ensures that dynamic occurs in thermal deformation process for alloy again
Crystallization, moreover it is possible to ensure that alloy has stable deformation mechanism.
(3) present invention can obtain the excellent aluminium alloy converted products of comprehensive mechanical property, high in machining efficiency, highly practical,
It is easy to spread.
Brief description of the drawings
Fig. 1 is the true stress-true strain curve map under the conditions of different distortion：Wherein (a) 0.001s-1(b)0.01s-1(c)
0.1s-1(d)1s-1；
Hot working chart when Fig. 2 is true strain 0.9；
Fig. 3 is 400 DEG C/1s-1Under the conditions of ln θ-ε graphs of a relation；
Fig. 4 is 400 DEG C/1s-1Under the conditions ofGraph of a relation；
The hot working chart of dynamic recrystallization generating region is included when Fig. 5 is true strain 0.9；
Hot working chart comprising dynamic recrystallization generating region and contour rarefaction when Fig. 6 is true strain 0.9.
Embodiment
1. by taking Al- (5.0~6.0) Zn- (1.5~2.5) Mg- (2.0~3.0) Cu aluminium alloys as an example.The feeding from ingot casting,
Cylinder small sample needed for Vehicle Processing into thermal simulation experiment, specimen size are 10 × 15mm of Φ.Utilize Gleeble-3500 heat
Simulation test machine carries out thermal simulation orthogonal test to cylinder sample.Deformation temperature chooses 350-450 DEG C according to technic metal, strain
Speed chooses 0.001-1s-1, the orthogonal experiment of progress 5 × 4.Sample heating rate is 2 DEG C/s, reaches preset temperature insulation 3min
Afterwards uniform speed's isothermal hot compression test is carried out according to experimental program.When deflection reaches 60% (namely true strain is about 0.9)
Stop compression afterwards, and sample is quenched rapidly into the water.
2. the data obtained according to thermal simulation experiment, it is bent to draw true stress-true strain of the alloy under the conditions of different distortion
Line, as shown in Figure 1.
3. the hot working chart based on dynamic material model (DMM) is the important tool of optimized alloy thermal process parameter.
DMM models are pointed out, in hot procedure, the gross energy of material consumption can be divided into two parts：1. plastic deformation institute occurs for material
The energy of dissipation, this portion of energy are known as dissipation amount, are represented with G；2. the energy that Microstructure evolution consumes in material deformation process
Amount, referred to as dissipation association are measured, and are represented with J.Two-part energy expenditure can be used to lower mathematical expression expression：
In formula, P is general power, and σ is flow stress,Strain rate is represented, G represents dissipation amount, and J represents dissipation association amount.
In addition, the flow stress in hot procedure can be described by following formula：
In formula, it with material structure and the relevant constant of deformation temperature, m is the strain hardening and strain-rate sensitivity factor that k, which is,.
It is available with reference to expression formula 1 and expression formula 2：
When m is constant, expression formula 4 is just effective.In general, m values are as the change of deformation temperature and strain rate is in non-thread
Property change.As m=1, material is in ideal linearity states of dissipation, and dissipation association amount J reaches maximum Jmax, i.e.,：
By expression formula 4 and expression formula 5, a nondimensional parameter η is can obtain, η is power dissipation efficiency factor, is represented
The proportionate relationship for the energy collinearity dissipation energy that Microstructure evolution is dissipated, can be expressed as in thermal deformation process：
Power dissipation efficiency factor constitutes power dissipation figure with the change of deformation temperature and strain rate, it is in certain journey
Reflect the Microstructure Development mechanism of material on degree.
Although energy dissipation figure can reflect that material is micro- under certain variations amount, deformation temperature and strain rate to a certain extent
The situation of change of structure is seen, but it is not the sole indicator for evaluating materials hot working performance.Because material is in manuscript
Rheological Instability region, it is also possible to there is the higher energy consumption efficiency factor, so unstability figure must also be drawn, to determine material
Process unstability region.According to principle of maximum entropy, Rheological Instability criterionIt is represented by
Change of the unstability parameter under the conditions of different distortion constitutes the unstability figure of material, and wherein region of the ξ values less than 0 is
Rheological Instability region (i.e. shadow region in figure).With thermal simulation experiment data of the alloy in true strain 0.9, construct respectively
Both, are then superimposed by the power dissipation figure and unstability figure of alloy, you can hot working chart of the alloy in true strain 0.9 is obtained,
As shown in Figure 2.Digital representation power dissipation efficiency factor on isopleth, shadow region is Rheological Instability area in figure, shadow region
Overseas is hot-working place of safety.
4. work hardening rateBe characterize material flow stress it is important with one of strain variation speed
Parameter.Material can be obtained using work hardening rate processing method on the basis of true stress-true strain curve dynamic occurs again
The condition of crystallization.According to true stress-true strain curve, draw out successively ln θ-ε figures andCurve map.If ln θ-
ε figures there are flex point orFigure is there are minimum point (minimum value), then there occurs dynamic under this deformation condition for alloy
Recrystallization, and the corresponding strain of minimum point is the critical strain of dynamic recrystallization；IfFigure is without minimum point or most
Small value, then alloy dynamic recrystallization does not occur.
The first step for determining alloy dynamic recrystallization occurrence condition is obtained on true stress-true strain curve under each strain
Slope size.Due to actual true stress-true strain curve and rough, therefore need first be fitted it, fit equation it is general
It is as follows all over form：
In formula, σ is stress, and ε is strains, A, A1, A2, A3, A4, A5, B, B1, B2, B3, B4, B5, B6For undetermined coefficient.
In actual process, after true stress-true strain curve matching, directly curve is asked using origin softwares
Differential can obtain θ-ε curves, thus can draw ln θ-ε figures, such as Fig. 3.Ln θ-ε figures are continued to differentiate and can obtainedCurve map, such as Fig. 4.If the ln θ-ε figures obtained there are flex point orFigure there are minimum point (most
Small value), then alloy under this deformation condition there occurs dynamic recrystallization, and minimum point corresponding strain facing for dynamic recrystallization
Boundary strains；If ln θ-ε figures there is no flex point orWithout minimum point or minimum value, then alloy dynamic does not occur for figure again
Crystallization.Can dynamic recrystallization be drawn in hot working chart there is a situation where dynamic recrystallization according to alloy under each deformation condition
Generating region, you can obtain the hot working chart for including dynamic recrystallization generating region during true strain 0.9, such as Fig. 5.
5. the density of manuscript medium value contour line has material impact to the deformation mechanism of alloy.Because when alloy is waiting
When being worth deformation in the densely distributed region of contour line, the minor alteration of deformation parameter will be larger to the generation of the deformation mechanism of alloy
Influence, plastic deformation is unstable, is unfavorable for processing.On the contrary, alloy can in thermal deformation under conditions of equivalent contour line is sparse
Produce the rheological behaviour of stable state.Therefore, equivalent profile is selected in the lap of place of safety and dynamic recrystallization generating region
Region (the deformation temperature that line is sparse and power consumption values are higher：380-420 DEG C, strain rate：0.004-0.1s-1, power dissipation efficiency
The factor：0.28-0.34), the deformation condition corresponding to this region be Al- (5.0~6.0) Zn- (1.5~2.5) Mg- (2.0~
3.0) the optimum thermal process parameter of Cu alloys, such as Fig. 6.
Embodiment 1
Selected respectively in 400 DEG C/0.01s in Fig. 6 " being adapted to hot-working region "-1With 420 DEG C/0.01s-1Under the conditions of heat
Deformed sample carries out electron backscatter diffraction (EBSD) analysis.The result shows that：When alloy is respectively in 400 DEG C/0.01s-1With
420℃/0.01s-1Under the conditions of deform after, the distribution of the angle of orientation is presented closely similar feature, and high-angle boundary (HAGBs) or
The percentage of low-angle boundary (LAGBs) almost indifference.In 400 DEG C/0.01s-1Under, the percentage of HAGBs is 67.1%；
420℃/0.01s-1Under the conditions of, the percentage of HAGBs is 67.2%.Because the conjunction of subgrain is attributed to the fact that in the appearance of recrystal grain
And and high-angle boundary formation, therefore the percentage of high-angle boundary can reflect the occurrence degree of dynamic recrystallization.It is meanwhile small
The characteristic distributions and its percentage of angle grain boundary can reflect the substructure feature of alloy.Therefore, experimental result explanation：In Fig. 6
In in the range of " be adapted to hot-working region ", the appropriate change of deformation temperature will not produce the deformation mechanism of alloy big influence.
Embodiment 2
Selected respectively in 400 DEG C/0.01s in Fig. 6 " being adapted to hot-working region "-1With 400 DEG C/0.1s-1Under the conditions of thermal change
Sample after shape carries out electron backscatter diffraction (EBSD) analysis.The result shows that：When alloy is respectively in 400 DEG C/0.01s-1With 400
℃/0.1s-1Under the conditions of when deforming, closely similar feature, and high-angle boundary (HAGBs) or small angle is presented in the distribution of the angle of orientation
Spend the percentage almost indifference of crystal boundary (LAGBs).In 400 DEG C/0.01s-1Under, the percentage of HAGBs is 67.1%；400
℃/0.1s-1Under the conditions of, the percentage of HAGBs is 67.0%.Therefore, experimental result explanation：" it is adapted to hot-working area in figure 6
In the range of domain ", the appropriate change of strain rate will not produce the deformation mechanism of alloy big influence.
Embodiment 1 and embodiment 2 illustrate：Within " being adapted to hot-working region ", appropriate change of deformation parameter will not pairing
The deformation mechanism of gold is produced and significantly affected.That is, alloy can produce stable state under the deformation condition corresponding to this region
Rheological behaviour.
Embodiment 3
" it is adapted to hot-working region " in figure 6 to select respectively outside in 420 DEG C/1s-1With 450 DEG C/1s-1Under the conditions of thermal deformation
Sample afterwards carries out electron backscatter diffraction (EBSD) analysis.The result shows that：When alloy is respectively in 420 DEG C/1s-1With 450 DEG C/
1s-1Under the conditions of deform after, there are larger difference for the distribution characteristics of the angle of orientation.Meanwhile high-angle boundary (HAGBs) or low-angle are brilliant
The percentage on boundary (LAGBs) is also very different.In 420 DEG C/1s-1Under the conditions of, the percentage of HAGBs is 85.2%；And 450
℃/1s-1Under the conditions of, the percentage of HAGBs is 64.8%.This explanation is when alloy is respectively in 420 DEG C/1s-1With 450 DEG C/1s-1Under
During deformation, there are larger difference for its dynamic recrystallization degree and substructure feature.These experimental result explanations：In region II
In the range of, the smaller change of deformation parameter will produce the deformation mechanism of alloy large effect, and plastic deformation is unstable.
Embodiment 4
" it is adapted to hot-working region " in figure 6 to select respectively outside in 400 DEG C/0.001s-1With 420 DEG C/0.001s-1Condition
Sample after lower thermal deformation carries out electron backscatter diffraction (EBSD) analysis.The result shows that：When alloy respectively 400 DEG C/
0.001s-1With 420 DEG C/0.001s-1Under the conditions of deform after, there are larger difference for the distribution characteristics of the angle of orientation.Meanwhile wide-angle
The percentage of crystal boundary (HAGBs) or low-angle boundary (LAGBs) is also very different.In 400 DEG C/0.001s-1Under the conditions of,
The percentage of HAGBs is 72.4%；And in 420 DEG C/0.001s-1Under the conditions of, the percentage of HAGBs is 86.6%.This explanation is worked as
Alloy is respectively in 400 DEG C/0.001s-1With 420 DEG C/0.001s-1During lower deformation, its dynamic recrystallization degree and substructure feature
There are larger difference.
Example 3 and example 4 show：In " suitable hot-working region " outside, the smaller change of deformation parameter will be to alloy
Deformation mechanism produces large effect, and plastic deformation is unstable, is not suitable for hot-working.
Therefore, the present invention is by considering place of safety and instability area, dynamic recrystallization generating region, equivalent wheel in manuscript
The size of profile rarefaction and power consumption values determines the optimum thermal process parameter of alloy.Choose equivalent contour line it is sparse,
Power consumption values it is higher and occur dynamic recrystallization safety zone corresponding to deformation parameter be the optimum heat processing technique of alloy
Region shown in square frame in parameter, i.e. Fig. 6.
Claims (8)
- A kind of 1. method for optimizing aluminum alloy heat processing technology, it is characterised in that including：(1) aluminum alloy specimen is subjected to thermal modeling test, obtains thermal simulation experiment data；(2) according to the thermal simulation experiment data, hot working chart is drawn by interpolation and the method for matrixing；(3) true stress-true strain curve is drawn according to the thermal simulation experiment data, is determined by work hardening rate processing method The condition of dynamic recrystallization occurs for alloy, and dynamic recrystallization generation area is drawn in hot working chart；(4) the equivalent area that contour line is sparse and power consumption values are higher is selected in place of safety and dynamic recrystallization generating region lap Domain, the deformation condition corresponding to this region are the optimum thermal process parameter of alloy.
- 2. the method as described in claim 1, it is characterised in that the aluminum alloy specimen is Al-Zn-Mg-Cu systems alloy.
- 3. the method for optimization aluminum alloy heat processing technology as claimed in claim 1, it is characterised in that the ruler of the aluminum alloy specimen Very little is 10 × 15mm of Φ.
- 4. the method for optimization aluminum alloy heat processing technology as claimed in claim 1, it is characterised in that in the thermal simulation experiment, Deformation temperature is 350-450 DEG C, strain rate 0.001-1s-1。
- 5. the method for optimization aluminum alloy heat processing technology as claimed in claim 1, it is characterised in that the hot working chart is by leading to The power dissipation figure and unstability figure for crossing the acquisition of thermal simulation experiment data are superimposed and obtain.
- 6. the method for optimization aluminum alloy heat processing technology as claimed in claim 1, it is characterised in that the work hardening rate processing Method is：On the basis of true stress-true strain curve, draw out successively ln θ-ε figure andCurve map, wherein θ refer to work hardening rate andε refers to strain.
- 7. the method for optimization aluminum alloy heat processing technology as claimed in claim 1, it is characterised in that the step of the thermal simulation experiment Suddenly it is：First pass through thermocouple and sample is heated to preset temperature with the heating rate of (2-10) DEG C/s, pressed after keeping the temperature (3-5) min Uniform speed's isothermal hot compression test is carried out according to experimental program.Stop compression after deflection reaches (50-60) %, sample is rapid Quench into the water.
- A kind of 8. aluminium alloy processing method, it is characterised in that including：Aluminum alloy specimen is analyzed according to the method any one of claim 1-7, acquisition includes dynamic accordingly State recrystallizes the hot working chart of generation area；According to the above-mentioned hot working chart for including dynamic recrystallization generation area, select equivalent contour line is sparse, power consumption values compared with Deformation Parameters corresponding to safety zone high and that dynamic recrystallization occurs are processed aluminum alloy materials.
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| CN108857132B (en) * | 2018-07-24 | 2021-04-20 | 哈尔滨工业大学（深圳） | Method for evaluating reliability of lead-free welding spot |
| CN109811115A (en) * | 2019-01-31 | 2019-05-28 | 武汉科技大学 | A kind of determination method of bainitic steel heat forming technology window |
| CN109856180A (en) * | 2019-01-31 | 2019-06-07 | 武汉科技大学 | A kind of Boron Bearing Microalloy Steel heat forming technology determination method for parameter |
| CN110849801A (en) * | 2019-11-29 | 2020-02-28 | 西北有色金属研究院 | Method for determining critical stress of metal low-speed deformation recrystallization |
| CN110899357A (en) * | 2019-12-09 | 2020-03-24 | 上海交通大学 | Hot processing method of industrial pure aluminum |
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