CN108595827A - A kind of determination method of C-Mn-Al high strength steels Hot Deformation Microstructure evolution mechanism and hot-working character - Google Patents
A kind of determination method of C-Mn-Al high strength steels Hot Deformation Microstructure evolution mechanism and hot-working character Download PDFInfo
- Publication number
- CN108595827A CN108595827A CN201810360313.6A CN201810360313A CN108595827A CN 108595827 A CN108595827 A CN 108595827A CN 201810360313 A CN201810360313 A CN 201810360313A CN 108595827 A CN108595827 A CN 108595827A
- Authority
- CN
- China
- Prior art keywords
- deformation
- hot
- strain
- stress
- model
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Pending
Links
- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 45
- 239000010959 steel Substances 0.000 title claims abstract description 45
- 238000000034 method Methods 0.000 title claims abstract description 36
- 230000007246 mechanism Effects 0.000 title claims abstract description 26
- 229910018657 Mn—Al Inorganic materials 0.000 title claims description 21
- 238000012545 processing Methods 0.000 claims abstract description 48
- 238000009792 diffusion process Methods 0.000 claims abstract description 11
- 229910001566 austenite Inorganic materials 0.000 claims abstract description 8
- 238000002474 experimental method Methods 0.000 claims abstract description 5
- 239000000463 material Substances 0.000 claims description 37
- 238000010586 diagram Methods 0.000 claims description 25
- 230000004913 activation Effects 0.000 claims description 3
- 230000006835 compression Effects 0.000 claims description 3
- 238000007906 compression Methods 0.000 claims description 3
- 238000012417 linear regression Methods 0.000 claims description 3
- 238000002844 melting Methods 0.000 claims description 3
- 230000008018 melting Effects 0.000 claims description 3
- 125000004432 carbon atom Chemical group C* 0.000 claims description 2
- 238000005516 engineering process Methods 0.000 abstract description 2
- 238000001953 recrystallisation Methods 0.000 description 14
- 230000008569 process Effects 0.000 description 8
- 239000007769 metal material Substances 0.000 description 7
- 238000011084 recovery Methods 0.000 description 5
- 238000011160 research Methods 0.000 description 4
- 230000007547 defect Effects 0.000 description 3
- 230000002427 irreversible effect Effects 0.000 description 3
- 238000003754 machining Methods 0.000 description 3
- 229910052710 silicon Inorganic materials 0.000 description 3
- 238000004088 simulation Methods 0.000 description 3
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 description 2
- 229910045601 alloy Inorganic materials 0.000 description 2
- 239000000956 alloy Substances 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 238000011156 evaluation Methods 0.000 description 2
- 239000010703 silicon Substances 0.000 description 2
- 229910018125 Al-Si Inorganic materials 0.000 description 1
- 229910018520 Al—Si Inorganic materials 0.000 description 1
- 229910018643 Mn—Si Inorganic materials 0.000 description 1
- 229910000794 TRIP steel Inorganic materials 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 229910001567 cementite Inorganic materials 0.000 description 1
- 230000008859 change Effects 0.000 description 1
- 239000011248 coating agent Substances 0.000 description 1
- 238000000576 coating method Methods 0.000 description 1
- 238000012669 compression test Methods 0.000 description 1
- 238000001816 cooling Methods 0.000 description 1
- 230000001687 destabilization Effects 0.000 description 1
- 238000011161 development Methods 0.000 description 1
- 230000008030 elimination Effects 0.000 description 1
- 238000003379 elimination reaction Methods 0.000 description 1
- 238000013210 evaluation model Methods 0.000 description 1
- 230000009931 harmful effect Effects 0.000 description 1
- 230000006872 improvement Effects 0.000 description 1
- KSOKAHYVTMZFBJ-UHFFFAOYSA-N iron;methane Chemical compound C.[Fe].[Fe].[Fe] KSOKAHYVTMZFBJ-UHFFFAOYSA-N 0.000 description 1
- 230000008707 rearrangement Effects 0.000 description 1
- 230000009467 reduction Effects 0.000 description 1
- 230000000717 retained effect Effects 0.000 description 1
Classifications
-
- G—PHYSICS
- G06—COMPUTING; CALCULATING OR COUNTING
- G06F—ELECTRIC DIGITAL DATA PROCESSING
- G06F30/00—Computer-aided design [CAD]
- G06F30/20—Design optimisation, verification or simulation
-
- G—PHYSICS
- G06—COMPUTING; CALCULATING OR COUNTING
- G06F—ELECTRIC DIGITAL DATA PROCESSING
- G06F30/00—Computer-aided design [CAD]
- G06F30/10—Geometric CAD
- G06F30/17—Mechanical parametric or variational design
Landscapes
- Engineering & Computer Science (AREA)
- Physics & Mathematics (AREA)
- Theoretical Computer Science (AREA)
- Geometry (AREA)
- General Physics & Mathematics (AREA)
- Evolutionary Computation (AREA)
- General Engineering & Computer Science (AREA)
- Computer Hardware Design (AREA)
- Computational Mathematics (AREA)
- Mathematical Analysis (AREA)
- Mathematical Optimization (AREA)
- Pure & Applied Mathematics (AREA)
- Investigating Strength Of Materials By Application Of Mechanical Stress (AREA)
Abstract
The invention belongs to high strength steel processing engineering technology field, more particularly to the determination method of a kind of C Mn Al high strength steel Hot Deformation Microstructure evolution mechanisms and hot-working character.The present invention carries out high temperature compressed experiment to novel C Mn Al high strength steels first, obtain the true stress-true stain curve data of steel, then the flow stress prediction model of steel is established, model selects based on creep theory, considers the self-diffusion coefficient of Young's modulus and austenite and constitutive model of the one kind with physical basis of temperature relation, the flow stress of the constitutive model energy Accurate Prediction steel of foundation；The thermal deformation manuscript for establishing steel determines the microstructure evolution mechanism of different zones in manuscript in conjunction with microscopic structure.Thermal deformation constitutive model and manuscript are combined, thermal deformation flow stress under the conditions of analysis random variation and thermal deformation power dissipation efficiency, to obtain corresponding microstructure evolution mechanism and hot-working character information, as a result high strength steel hot procedure is controlled significant.
Description
Technical Field
The invention belongs to the technical field of high-strength steel processing engineering, and particularly relates to a C-Mn-Al high-strength steel thermal deformation structure evolution mechanism and a method for determining thermal processing performance.
Background
In order to save energy and protect the environment, the development of high strength steel having good ductility and toughness, including TRIP steel, is urgently required. Conventional TRIP steels have been developed based on the C-Mn-Si alloy system, and the purpose of using a high silicon content is to suppress the formation of cementite during cooling so as to increase the stability and amount of retained austenite. However, high silicon content may cause defects in the steel, such as a hard oxide layer, poor surface properties and low coating ability. Since Al replaces Si to eliminate these harmful effects of Si, C-Mn-Al-Si or C-Mn-Al based TRIP steels have attracted more and more attention, and a great deal of research on the microstructure and mechanical behavior of such steels has been conducted, but the research on the thermal deformation behavior is relatively lacking.
Dynamic recrystallization is a very common and important deformation mechanism, during the dynamic recrystallization process, obvious tissue reconstruction occurs, various defects in an original tissue can be greatly eliminated, and the microscopic tissue change leads to the improvement of macroscopic processing plasticity and the reduction of deformation resistance. Dynamic recovery always occurs in the early stage of the dynamic recrystallization process, because elimination and rearrangement of dislocation occurring in the dynamic recovery process can form a cell structure with a certain size and an interface with poor large angle orientation, which is the condition for providing a new core for dynamic recrystallization. Dynamic recrystallization is a safe deformation mechanism in the hot working process, and in order to obtain a good thermal deformation microstructure, deformation parameters are controlled to be in a range where the dynamic recrystallization mechanism of the alloy plays a role as much as possible when a hot working process is established.
The constitutive equation of thermal deformation can express the relationship among physical quantities such as stress, strain, temperature and strain rate, which can be measured on a macroscopic object. The constitutive equation has the advantages that the rheological stress under a certain deformation condition can be intuitively obtained, but the structure evolution mechanism and the hot working performance of the material cannot be determined simply through the information of a rheological stress curve. The dynamic material model is established according to the fundamental principles of irreversible thermophysics, physical system simulation, continuous mechanics and the like under the condition of large-strain plastic deformation. The processing diagram of the dynamic material model can accurately reflect the tissue evolution law and mechanism of the material under different deformation conditions through a small amount of experiments, and further can be used for optimizing the thermal processing technology of the material, but the information of the rheological stress curve can not be obtained through the processing diagram.
Through search, the chinese patent application No. 201610131725.3 discloses a method for evaluating hot workability of a metal material, the method comprising the steps of: (1) performing a high-temperature compression test on the metal material under the designed thermal deformation condition to obtain true stress-true strain data of the metal material; (2) establishing an improved hyperbolic sine constitutive model for describing the high-temperature rheological stress of the metal material, and realizing the hyperbolic sine constitutive model through programming; (3) establishing a metal material hot working dissipation efficiency evaluation model and a instability criterion model, and realizing the evaluation through programming; (4) by adopting the model for predicting the high-temperature rheological stress, the model for evaluating the thermal processing dissipation efficiency and the instability criterion model which are established in the steps (2) and (3), the rheological stress, the thermal processing dissipation efficiency and the instability coefficient of the metal material under any deformation condition can be predicted, so that the comprehensive evaluation of the thermal processing performance of the metal material under any deformation condition is realized. However, the application still adopts the traditional hyperbolic sine constitutive model, and the accuracy of the prediction result still needs to be further improved.
Disclosure of Invention
1. Technical problem to be solved by the invention
The invention aims to overcome the defects of the prior art and provides a method for determining the evolution mechanism and the hot-working performance of the hot deformation structure of C-Mn-Al high-strength steel. The method can more accurately judge the heat deformation structure evolution mechanism and the hot working performance of the C-Mn-Al high-strength steel under different conditions, and has important guiding significance for reasonably formulating the hot working process of the C-Mn-Al high-strength steel.
2. Technical scheme
In order to achieve the purpose, the technical scheme provided by the invention is as follows:
the invention discloses a method for determining a thermal deformation structure evolution mechanism and a thermal processing performance of C-Mn-Al high-strength steel, which comprises the following steps:
step 1: carrying out high-temperature compression experiments on the steel at different deformation temperatures and strain rates to obtain true stress-true strain curve data of the steel;
step 2: establishing a constitutive model for predicting the high-temperature rheological stress of the C-Mn-Al high-strength steel, wherein the constitutive model is selected from a class of models with physical basis based on a creep theory and considering the relationship between the Young modulus and the self-diffusion coefficient of austenite and the temperature, and is shown as the following formula:
in the above formula, the first and second carbon atoms are,is the strain rate(s)-1) T is temperature (K), σ is rheological stress (MPa), D (T) is the self-diffusion coefficient of austenite, and D (T) ═ D0exp(Qsd/(RT))，D0Is the diffusion constant, Qsdis self-diffusion activation energy, E (T) describes the relationship between Young's modulus and temperature, B', α 'and n' are material constants;
introducing the influence of the strain epsilon on the rheological stress of the experimental steel into a constitutive equation, calculating the constitutive equations under the stress corresponding to different strains of a series one by one, and fitting the obtained relationship between the material constants lnB ', α ' and n ' and the strain epsilon by using a 5 th-order polynomial;
and substituting the fitting result into the model to obtain a rheological stress prediction model:
wherein α'ε＝α0+α1ε+α2ε2+α3ε3+α4ε4+α5ε5，n′ε＝N0+N1ε+N2ε2+N3ε3+N4ε4+N5ε5，(lnB′)ε＝B0′+B1′ε+B2′ε2+B3′ε3+B4′ε4+B5′ε5；
and 3, establishing a dynamic material model according to the fundamental principles of irreversible thermophysics, physical system simulation, continuous mechanics and the like under the condition of large-strain plastic deformation, wherein the criterion for defining the power dissipation efficiency factor η and the processing instability is as follows according to the dynamic material model:
where m is the strain rate sensitive factor,under the same strain, drawing an η contour map, namely a power dissipation map, and drawing a region with a negative parameter ξ, namely a hot processing instability map, on a two-dimensional plane of temperature-strain rate to obtain a processing map of the material;
and 4, combining the constitutive model and the processing diagram to research the thermal deformation behavior of the material, namely predicting stress-strain curves under different deformation conditions by using the established constitutive model, determining power dissipation efficiency factors η under different deformation conditions corresponding to different positions in the processing diagram, and thus obtaining rheological stress curve information and thermal deformation power dissipation efficiency η values under any deformation conditions.
Furthermore, the deformation temperature in the step 1 is 900-1100 ℃, the interval of the deformation temperature is 50 ℃, and the strain rate is 0.01-30s-1Respectively taking 0.01, 0.1, 1, 10 and 30s-1。
further, the value of α ' in step 2 is represented by the formula α ' ═ β '/n1' obtaining, and n1'and β' are respectively composed ofAndobtaining the slope of (a), obtaining n from linear regression1values of 'and' linear fitting according to a constitutive modelThe resulting slope and intercept are used to calculate the values of n 'and lnB', respectively.
Furthermore, in the step 2, the value of the strain epsilon ranges from 0.05 to 0.80, and the interval is 0.05.
Further, E (T) in step 2 is calculated according to the following formula:
wherein E is0And G0Respectively represents the Young modulus and the shear modulus of the material at 300K, G is the shear modulus of the material at the temperature T, and T isMIs the melting point of the material.
3. Advantageous effects
Compared with the prior art, the technical scheme provided by the invention has the following remarkable effects:
(1) the method for determining the evolution mechanism and the hot processing performance of the hot deformed structure of the C-Mn-Al high-strength steel combines a physical hot deformation constitutive equation and a physical hot deformation processing diagram, and mutually verifies the two methods of the processing diagram and the constitutive equation, so that the evolution mechanism and the hot processing performance of the hot deformed structure under different conditions can be more accurately judged.
(2) the invention relates to a method for determining a C-Mn-Al high-strength steel thermal deformation structure evolution mechanism and thermal processing performance, which predicts stress-strain curves under different deformation conditions by using an established constitutive model, determines power dissipation efficiency factors η under different deformation conditions corresponding to different positions in a processing diagram, thereby obtaining rheological stress curve information and thermal deformation power dissipation efficiency η values under any deformation conditions, and knows thermal deformation and dynamic recrystallization information of a material under a certain deformation condition, thereby providing important reference for the thermal processing process of the material.
Drawings
Fig. 1-4 are comparison of predicted values and experimental values of a constitutive model under different deformation conditions.
FIG. 5 is a heat distortion processing drawing and a heat distortion microstructure corresponding to different regions in the processing drawing.
FIG. 6 shows two different deformation conditions (1080 ℃ C., 0.03 s)-1At 930 ℃ for 6s-1) And (5) calibrating the position in the corresponding machining diagram.
FIG. 7 shows the temperature at 1080 ℃ for 0.03s-1The rheological stress curve predicted by the constitutive model under the condition.
FIG. 8 shows the temperature at 930 ℃ for 6s-1The rheological stress curve predicted by the constitutive model under the condition.
Detailed Description
For a further understanding of the invention, reference will now be made in detail to specific embodiments of the invention.
Example 1
The method for determining the hot deformation structure evolution mechanism and the hot working performance of the C-Mn-Al high-strength steel comprises the following steps:
step 1: at a deformation temperature of 900-1100 deg.C (interval of 50 deg.C) and a strain rate of 0.01-30s-1(0.01、0.1、1、10、30s-1) Performing a high-temperature compression experiment on the C-Mn-Al high-strength steel under the thermal deformation condition with the strain capacity of 0.6 of engineering strain to obtain true stress-true strain curve data of the C-Mn-Al high-strength steel;
step 2: establishing a constitutive model for predicting the thermal deformation rheological stress of the C-Mn-Al high-strength steel, wherein the selected constitutive equation is as follows:
wherein,is the strain rate(s)-1) where T is temperature (K), σ is rheological stress (MPa), B ', α ', and n ' are material constants, D (T) is the self-diffusion coefficient of austenite, and D (T) ═ D0exp(Qsd/(RT))，D0Is the diffusion constant, QsdIs the self-diffusion activation energy, E (T) describes the Young's modulus as a function of temperature. gamma-Fe is the closest material to the experimental steel, and the data of gamma-Fe is substituted to obtain:
wherein E is0And G0Respectively representing the Young's modulus and shear modulus, T, of the material at 300KMIs the melting point of the material.
the value of α ' can be determined using the formula α ' ═ β '/n1' obtaining, and n1'and β' may be respectively composed ofAndobtaining the slope of (1) and linear regression to obtain n1values of β 'and β' Linear fitting according to the constitutive equationThe resulting slope and intercept can be used to calculate the values of n 'and lnB', respectively.
introducing the influence of the strain on the rheological stress of the experimental steel into a constitutive equation, wherein the value of the strain is from 0.05 to 0.80, the interval is 0.05, calculating the constitutive equations under the stress corresponding to different strains of a series one by one, and fitting the obtained relationship between the material constants α ', n ' and lnB ' and the strain epsilon by using a 5-degree polynomial.
Substituting the coefficient values obtained by fitting into an equation to obtain a physical-based rheological stress prediction model:
wherein, α'ε＝α0+α1ε+α2ε2+α3ε3+α4ε4+α5ε5，n′ε＝N0+N1ε+N2ε2+N3ε3+N4ε4+N5ε5，(lnB′)ε＝B0′+B1′ε+B2′ε2+B3′ε3+B4′ε4+B5′ε5The coefficients are shown in Table 1.
The thermal deformation rheological stress under different deformation conditions is calculated by using the prediction model, and the comparison graph of the obtained predicted value and the experimental value is shown in figures 1-4.
TABLE 1 values of the respective coefficients in the fifth order polynomial
and 3, establishing a dynamic material model according to the fundamental principles of irreversible thermophysics, physical system simulation, continuous mechanics and the like under the condition of large-strain plastic deformation, and defining a power dissipation efficiency factor η and a processing instability criterion according to the dynamic material model.
Where m is the strain rate sensitive factor,under the same strain, on a two-dimensional plane of temperature-strain rate, an η contour map (namely a power dissipation map) is drawn, and then a parameter xi is drawn to be about negativeThe area (i.e., the hot working instability map) of (i.e., the material is obtained.
In order to verify the accuracy of the hot deformation processing diagram, the structure of the steel under different deformation conditions is observed, and a rheological instability region, a dynamic recrystallization region and a dynamic recovery region in the processing diagram are determined by combining the structure with the processing diagram. FIG. 5 shows the obtained processing diagram and the microstructure diagram corresponding to different regions in the processing diagram, wherein the shadow region in the diagram can be determined as the processing destabilization region (should avoid the thermal processing in the region), and the rectangular frame line in the diagram includes the region (1000-1100 deg.C, 0.01-1 s)-1) The dynamic recrystallization region and the other regions are dynamic recovery regions.
And 4, step 4: the heat distortion behavior of the material was studied by combining the constitutive equation with the processing diagram: and predicting stress-strain curves under different deformation conditions by using the established constitutive equation. Different deformation conditions correspond to different locations in the process map, with different power dissipation efficiencies. The two methods of the processing diagram and the constitutive equation can be mutually verified, and the tissue evolution mechanism and the hot processing performance of different deformation conditions can be more accurately judged. The following examples will be specifically described.
Two different deformation conditions (1080 ℃ C., 0.03 s) were arbitrarily selected-1At 930 ℃ for 6s-1) The analysis was performed as an example. The results are shown in the processing diagram (1080 ℃ C., 0.03 s)-1At 930 ℃ for 6s-1) In the position shown in figure 6. As can be seen from fig. 3: 1080 ℃ and 0.03s-1The deformation condition (2) corresponds to a power dissipation efficiency of 0.25 in the dynamic recrystallization region at 930 ℃ for 6s-1The deformation condition (2) corresponds to a power dissipation efficiency of 0.19 in the dynamic recovery region. The stress-strain curves under two deformation conditions predicted by the constitutive equation are shown in fig. 7 and 8. It can be seen that the temperature is 1080 ℃ for 0.03s-1The flow stress curve under the deformation condition is in a dynamic recrystallization type, so that the dynamic recrystallization of the material under the deformation condition is judged by both methods of a processing diagram and a constitutive equation. And at 930 ℃ for 6s-1The rheological stress curve under the deformation condition has no obvious dynamic recrystallization peak value, so the deformation is preliminarily judgedsimilarly, the method can be used for obtaining the rheological stress curve information and the thermal deformation power dissipation efficiency η value under any deformation condition, thereby determining the thermal deformation structure evolution mechanism and the thermal processing performance of the material.
The method predicts the rheological stress curve of the steel by selecting a novel physical-based constitutive model, and compared with the traditional hyperbolic sine constitutive model, the method is simple and effective and has a certain physical basis. According to the method, the prediction result of the constitutive model and the analysis result of the machining diagram are compared and researched, and the research result further confirms that the hot working behavior of the steel can be more effectively predicted by the cooperation of the constitutive model and the machining diagram. In summary, by combining the processing diagram and the constitutive equation, the thermal deformation and dynamic recrystallization information under a certain deformation condition can be comprehensively known, thereby providing an important reference for the material thermal processing process.
Claims (5)
1. A method for determining a hot deformation structure evolution mechanism and hot working performance of C-Mn-Al high-strength steel is characterized by comprising the following steps:
step 1: carrying out high-temperature compression experiments on the steel at different deformation temperatures and strain rates to obtain true stress-true strain curve data of the steel;
step 2: establishing a constitutive model for predicting the high-temperature rheological stress of the C-Mn-Al high-strength steel, which is shown as the following formula:
in the above formula, the first and second carbon atoms are,is the strain rate(s)-1) T is temperature (K), σ is rheological stress (MPa), D (T) is the self-diffusion coefficient of austenite, and D (T) ═ D0exp(Qsd/(RT))，D0Is the diffusion constant, Qsdis self-diffusion activation energy, E (T) describes the relationship between Young's modulus and temperature, B', α 'and n' are material constants;
introducing the influence of the strain epsilon on the rheological stress of the experimental steel into a constitutive equation, calculating the constitutive equations under the stress corresponding to different strains of a series one by one, and fitting the obtained relationship between the material constants lnB ', α ' and n ' and the strain epsilon by using a 5 th-order polynomial;
and substituting the fitting result into the model to obtain a rheological stress prediction model:
wherein α'ε＝α0+α1ε+α2ε2+α3ε3+α4ε4+α5ε5，n′ε＝N0+N1ε+N2ε2+N3ε3+N4ε4+N5ε5，(lnB′)ε＝B′0+B′1ε+B′2ε2+B′3ε3+B′4ε4+B′5ε5；
step 3, defining the criterion of the power dissipation efficiency factor η and the processing instability according to the dynamic material model as follows:
wherein m is a strain rate sensitive factor, and an eta contour map, namely a power dissipation map, is drawn on a two-dimensional plane of temperature-strain rate under the same strain, and a region with a negative parameter ξ, namely a hot processing instability map, is drawn to obtain a processing map of the material;
and 4, combining the constitutive model and the processing diagram to study the thermal deformation behavior of the material, namely predicting stress-strain curves under different deformation conditions by using the established constitutive model, determining power dissipation efficiency factors η under different deformation conditions corresponding to different positions in the processing diagram, so as to obtain rheological stress curve information and thermal deformation power dissipation efficiency η values under any deformation conditions, and further determining a thermal deformation structure evolution mechanism and thermal processing performance of the material.
2. The method for determining the heat deformation structure evolution mechanism and the hot working performance of the C-Mn-Al high-strength steel according to claim 1, wherein the method comprises the following steps: the deformation temperature in the step 1 is 900-1100 ℃, the interval of the deformation temperature is 50 ℃, and the strain rate is 0.01-30s-1Respectively taking 0.01, 0.1, 1, 10 and 30s-1。
3. the method for determining the heat deformation structure evolution mechanism and the hot working performance of the C-Mn-Al high-strength steel according to claim 1, wherein the value of α 'in the step 2 is represented by the formula α' ═ β '/n'1To obtain n'1and β' are respectively composed ofAndslope of (2)To obtain n 'from linear regression'1and beta' values, linear fitting according to a constitutive modelThe resulting slope and intercept are used to calculate the values of n 'and ln B', respectively.
4. The method for determining the heat deformation structure evolution mechanism and the hot working performance of the C-Mn-Al high-strength steel according to any one of claims 1 to 3, wherein the method comprises the following steps: in the step 2, the value of the strain epsilon ranges from 0.05 to 0.80, and the interval ranges from 0.05.
5. The method for determining the heat deformation structure evolution mechanism and the hot working performance of the C-Mn-Al high-strength steel according to any one of claims 1 to 3, wherein the method comprises the following steps: e (T) in step 2 is calculated according to the following formula:
wherein E is0And G0Respectively represents the Young modulus and the shear modulus of the material at 300K, G is the shear modulus of the material at the temperature T, and T isMIs the melting point of the material.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201810360313.6A CN108595827A (en) | 2018-04-20 | 2018-04-20 | A kind of determination method of C-Mn-Al high strength steels Hot Deformation Microstructure evolution mechanism and hot-working character |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201810360313.6A CN108595827A (en) | 2018-04-20 | 2018-04-20 | A kind of determination method of C-Mn-Al high strength steels Hot Deformation Microstructure evolution mechanism and hot-working character |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| CN108595827A true CN108595827A (en) | 2018-09-28 |
Family
ID=63614351
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN201810360313.6A Pending CN108595827A (en) | 2018-04-20 | 2018-04-20 | A kind of determination method of C-Mn-Al high strength steels Hot Deformation Microstructure evolution mechanism and hot-working character |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN108595827A (en) |
Cited By (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN109492332A (en) * | 2018-12-11 | 2019-03-19 | 西安交通大学 | For the analogy method of the single component thermal deformation of sodium-cooled fast reactor |
| 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 |
| CN110096759A (en) * | 2019-04-10 | 2019-08-06 | 西北工业大学 | Blade of aviation engine mechanical property appraisal procedure and device |
| CN110570910A (en) * | 2019-08-19 | 2019-12-13 | 华中科技大学 | Method and system for reducing dislocation density of growing gallium nitride film |
| CN110705108A (en) * | 2019-10-08 | 2020-01-17 | 天津理工大学 | Method for determining hot working temperature range of low-alloy high-strength steel for ocean engineering |
| CN111380899A (en) * | 2019-11-29 | 2020-07-07 | 中国科学院金属研究所 | Method for correcting zirconium alloy flow stress through rolling simulation process temperature rise |
| CN111735715A (en) * | 2020-06-28 | 2020-10-02 | 苏州健雄职业技术学院 | PLC effect micro-mechanism test method of CHDG-A austenitic heat-resistant steel |
| CN112729376A (en) * | 2020-11-27 | 2021-04-30 | 成都先进金属材料产业技术研究院有限公司 | Method for evaluating hot working performance of light high-strength steel |
Citations (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS61270332A (en) * | 1985-05-27 | 1986-11-29 | Mitsubishi Heavy Ind Ltd | Thermo-mechanical treatment of austenitic stainless steel |
| JPH04110417A (en) * | 1990-08-31 | 1992-04-10 | Minoru Umemoto | Method for predicting austenitic structure in steel after multi-pass hot-working |
| CN103852382A (en) * | 2014-03-04 | 2014-06-11 | 湖南大学 | Establishment method of high-strength steel plate thermoforming limit diagram |
| CN104928605A (en) * | 2015-07-20 | 2015-09-23 | 中南大学 | Method for predicting nickel base alloy high temperature flow stress and dynamic recrystallization behavior |
| CN104951633A (en) * | 2015-07-20 | 2015-09-30 | 中南大学 | Method for predicting work-hardening and dynamic recovery behaviors of nickel-based alloy |
| CN105651620A (en) * | 2016-03-09 | 2016-06-08 | 中南大学 | Method estimating hot-working performance of metal material |
| CN107121992A (en) * | 2017-03-28 | 2017-09-01 | 华南理工大学 | A kind of strong rotation shape/property integrated control method of cylindrical member heat based on hot working chart |
-
2018
- 2018-04-20 CN CN201810360313.6A patent/CN108595827A/en active Pending
Patent Citations (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS61270332A (en) * | 1985-05-27 | 1986-11-29 | Mitsubishi Heavy Ind Ltd | Thermo-mechanical treatment of austenitic stainless steel |
| JPH04110417A (en) * | 1990-08-31 | 1992-04-10 | Minoru Umemoto | Method for predicting austenitic structure in steel after multi-pass hot-working |
| CN103852382A (en) * | 2014-03-04 | 2014-06-11 | 湖南大学 | Establishment method of high-strength steel plate thermoforming limit diagram |
| CN104928605A (en) * | 2015-07-20 | 2015-09-23 | 中南大学 | Method for predicting nickel base alloy high temperature flow stress and dynamic recrystallization behavior |
| CN104951633A (en) * | 2015-07-20 | 2015-09-30 | 中南大学 | Method for predicting work-hardening and dynamic recovery behaviors of nickel-based alloy |
| CN105651620A (en) * | 2016-03-09 | 2016-06-08 | 中南大学 | Method estimating hot-working performance of metal material |
| CN107121992A (en) * | 2017-03-28 | 2017-09-01 | 华南理工大学 | A kind of strong rotation shape/property integrated control method of cylindrical member heat based on hot working chart |
Non-Patent Citations (5)
| Title |
|---|
| 潘红波等: "低碳硅锰钢奥氏体区形变对贝氏体组织及力学性能影响", 《金属热处理》 * |
| 魏海莲: "中低碳微合金钢及C-Mn-Al（Si）高强钢的热变形行为研究", 《中国优秀博硕士学位论文全文数据库（博士）工程科技I辑》 * |
| 魏海莲等: "基于本构分析的中碳钒微合金钢热变形行为", 《材料科学与工艺》 * |
| 魏海莲等: "新型微合金化C--Mn--Al高强度钢的热变形行为", 《北京科技大学学报》 * |
| 魏海莲等: "表观的和基于物理的35Mn2钢奥氏体热变形本构分析", 《金属学报》 * |
Cited By (10)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN109492332A (en) * | 2018-12-11 | 2019-03-19 | 西安交通大学 | For the analogy method of the single component thermal deformation of sodium-cooled fast reactor |
| 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 |
| CN110096759A (en) * | 2019-04-10 | 2019-08-06 | 西北工业大学 | Blade of aviation engine mechanical property appraisal procedure and device |
| CN110570910A (en) * | 2019-08-19 | 2019-12-13 | 华中科技大学 | Method and system for reducing dislocation density of growing gallium nitride film |
| CN110570910B (en) * | 2019-08-19 | 2021-10-08 | 华中科技大学 | Method and system for reducing dislocation density of growing gallium nitride film |
| CN110705108A (en) * | 2019-10-08 | 2020-01-17 | 天津理工大学 | Method for determining hot working temperature range of low-alloy high-strength steel for ocean engineering |
| CN111380899A (en) * | 2019-11-29 | 2020-07-07 | 中国科学院金属研究所 | Method for correcting zirconium alloy flow stress through rolling simulation process temperature rise |
| CN111735715A (en) * | 2020-06-28 | 2020-10-02 | 苏州健雄职业技术学院 | PLC effect micro-mechanism test method of CHDG-A austenitic heat-resistant steel |
| CN111735715B (en) * | 2020-06-28 | 2022-01-11 | 苏州健雄职业技术学院 | PLC effect micro-mechanism test method of CHDG-A austenitic heat-resistant steel |
| CN112729376A (en) * | 2020-11-27 | 2021-04-30 | 成都先进金属材料产业技术研究院有限公司 | Method for evaluating hot working performance of light high-strength steel |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN108595827A (en) | A kind of determination method of C-Mn-Al high strength steels Hot Deformation Microstructure evolution mechanism and hot-working character | |
| Zhao et al. | Evaluation of the deformation behaviors and hot workability of a high-strength low-alloy steel | |
| Li et al. | Constitutive equations for high temperature flow stress prediction of Al–14Cu–7Ce alloy | |
| Dong et al. | A physically-based constitutive model for SA508-III steel: modeling and experimental verification | |
| Chu et al. | Characterization of the elevated temperature compressive deformation behavior of high Nb containing TiAl alloys with two microstructures | |
| CN105586476B (en) | High-strength steel quenching technical optimization method based on numerical simulation technology | |
| Wang et al. | Influence of grain orientation on the incipient oxidation behavior of Haynes 230 at 900° C | |
| Bobbili et al. | Constitutive modeling of hot deformation behavior of high-strength armor steel | |
| Sun et al. | Constitutive relationship of IN690 superalloy by using uniaxial compression tests | |
| Wolla et al. | Constitutive modeling of powder metallurgy processed Al–4% Cu preforms during compression at elevated temperature | |
| Yu et al. | Application of four different models for predicting the high-temperature flow behavior of TG6 titanium alloy | |
| Lin et al. | A new creep constitutive model for 7075 aluminum alloy under elevated temperatures | |
| Liu et al. | The kinetics of dynamic recrystallization and construction of constitutive modeling of RAFM steel in the hot deformation process | |
| Churyumov et al. | Effect of boron concentration on hot deformation behavior of stainless steel | |
| Zhang et al. | Hot Deformation Behavior of an Ultra-High-Strength Fe–Ni–Co-Based Maraging Steel | |
| Wang et al. | Interdiffusion behaviors and mechanical properties in BCC Zr-rich Zr–Nb–Ta system | |
| CN106383928A (en) | Method for constructing high-temperature plastic flow densification constitutive models of powder sintering materials | |
| Sajadifar et al. | Dynamic recrystallization behavior and hot deformation characteristics in 4340 steel | |
| Jia et al. | Development of the dynamic globularization prediction model for Ti-17 titanium alloy using finite element method | |
| CN102750453B (en) | Construction method of material deformation resistance unified model for rolling mill design | |
| Wang et al. | Deformation behavior of TiNiFe alloy in isothermal compression | |
| Jia et al. | Microstructural evolution and constitutive models of 9CrMoCoB heat-resistant steel during high-temperature deformation | |
| Zhu et al. | Optimization of hot deformation parameters for multi-directional forging of Ti65 alloy based on the integration of processing maps and finite element method | |
| Li et al. | Deformation behavior of powder metallurgy connecting rod preform during Hot forging based on Hot compression and finite element method simulation | |
| Huang et al. | Dynamic recrystallization behavior and texture evolution of NiAl intermetallic during hot deformation |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| PB01 | Publication | ||
| PB01 | Publication | ||
| SE01 | Entry into force of request for substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| RJ01 | Rejection of invention patent application after publication |
Application publication date: 20180928 |
|
| RJ01 | Rejection of invention patent application after publication |