CN107423469B - Method for judging complete forging of 06Cr19Ni9NbN steel - Google Patents
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 98
- 239000010959 steel Substances 0.000 title claims abstract description 98
- 238000005242 forging Methods 0.000 title claims abstract description 54
- 238000000034 method Methods 0.000 title claims abstract description 40
- 238000001953 recrystallisation Methods 0.000 claims abstract description 56
- 238000004088 simulation Methods 0.000 claims abstract description 39
- 238000007906 compression Methods 0.000 claims abstract description 32
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- 238000005096 rolling process Methods 0.000 description 10
- 239000000463 material Substances 0.000 description 7
- 229910001220 stainless steel Inorganic materials 0.000 description 5
- 239000010935 stainless steel Substances 0.000 description 5
- 238000010586 diagram Methods 0.000 description 4
- 238000005260 corrosion Methods 0.000 description 3
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- 238000004519 manufacturing process Methods 0.000 description 1
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Abstract
The invention discloses a method for judging complete forging of 06Cr19Ni9NbN steel. The method comprises the following steps: after the 06Cr19Ni9NbN steel is subjected to plane strain compression, measuring the actual grain size and the actual dynamic recrystallization percentage of the 06Cr19Ni9NbN steel after compression; simulating the steel plane strain compression process by DEFORMMM to obtain the simulated grain size and simulated dynamic recrystallization percentage of the compressed 06Cr19Ni9NbN steel; adjusting simulation parameters to make the simulated crystal grain size consistent with the actual crystal grain size to obtain optimal simulation parameters; and under the condition of optimal simulation parameters, simulating the change rule of the strain and the dynamic recrystallization percentage of the steel at different temperatures according to DEFORMMM, establishing a forging through critical mathematical model of the steel, and when the forging through critical value is zero, indicating that the steel is forged through. The method is simple to operate, and can accurately judge whether the 06Cr19Ni9NbN steel is completely forged.
Description
Technical Field
The invention relates to the field of steel forging, in particular to a method for judging the forged penetration of 06Cr19Ni9NbN steel.
Background
06Cr19Ni9NbN is a novel austenitic stainless steel, which is prepared by adding a small amount of N and Nb elements on the basis of the existing 06Cr19Ni10 stainless steel, wherein the addition of the N element reduces the intergranular corrosion sensitivity of the stainless steel and improves the corrosion resistance of the steel, and the addition of the Nb element improves the high-temperature strength of the stainless steel. The stainless steel has strong antirust and corrosion resistance, better plasticity and toughness, and good high temperature resistance and processability of metal products, so that the stainless steel is widely applied to industries such as industry, food, medical treatment and the like. The material is single-phase austenitic stainless steel, cannot be strengthened by heat treatment, and can only refine grains by thermal deformation.
The 06Cr19Ni9NbN steel has complex structure evolution in the thermal deformation process, and the final mechanical property of the steel is influenced, so that the judgment of whether the material is completely forged in the forging process is very important for the final quality of the material. The forging penetration is the depth of the forging along the forging direction, and is mainly influenced by the tonnage of forging equipment, the size of a hammer head (also called an anvil), the forming speed, the material and other factors.
At present, the research on the forging through problem is mainly focused on upsetting, drawing and radial forging, and the judgment of the forging through critical value is mainly based on an empirical method, which lacks necessary quantitative analysis, is not closely connected with actual hot working, is inconvenient and inaccurate, and has no theoretical basis.
Disclosure of Invention
In view of this, the embodiment of the present invention provides a method for determining the forged-through of 06Cr19Ni9NbN steel, and mainly aims to solve the technical problem that whether the 06Cr19Ni9NbN steel is forged through cannot be accurately determined.
In order to achieve the purpose, the invention mainly provides the following technical scheme:
in one aspect, an embodiment of the present invention provides an identification method for a forged piece of 06Cr19Ni9NbN steel, including the following steps:
(1) performing plane strain compression on 06Cr19Ni9NbN steel, measuring the actual grain size of the compressed 06Cr19Ni9NbN steel and calculating the actual dynamic recrystallization percentage;
(2) simulating the 06Cr19Ni9NbN steel by using a finite element process simulation system DEFORMMM to perform a plane strain compression process under the condition that the compression process parameters are the same as those in the step (1), and obtaining the simulated grain size, the simulated dynamic recrystallization percentage and the change rule of the two of the compressed 06Cr19Ni9NbN steel;
(3) comparing the actual grain size with the simulated grain size, comparing the actual dynamic recrystallization percentage with the simulated dynamic recrystallization percentage, and adjusting the simulation parameters of the finite element process simulation system DEFORM to obtain the optimal simulation parameters of the DEFORM after the simulated grain size is the same as the actual grain size and the actual dynamic recrystallization percentage is the same as the simulated dynamic recrystallization percentage;
under the condition of the known optimal simulation parameters of the DEFORM, re-simulating the change rule of the simulated grain size and the simulated dynamic recrystallization percentage by using the DEFORM to obtain a forging critical model of the 06Cr19Ni9NbN steel:
wherein, omega is a forging critical value, and epsilon is strain;
z represents a temperature-compensated strain rate factor,
wherein,
for strain rate, T is temperature;
and when omega is zero, the 06Cr19Ni9NbN steel is completely forged, and the critical strain value of the 06Cr19Ni9NbN steel is completely forged according to a complete forging critical model.
Preferably, the forging critical model of the 06Cr19Ni9NbN steel is expressed by the following specific steps:
simulating the change rule of the simulated grain size and the simulated dynamic recrystallization percentage according to DEFORM to obtain a model expression of simulated strain and simulated dynamic recrystallization percentage:
εp＝0.0056Z0.117，
wherein, XdIs the dynamic recrystallization percentage, epsilon is the strain, epsilon p is the peak strain;
and the simulation dynamic recrystallization percentage is subjected to derivative calculation on the simulation strain to obtain a mathematical expression of the simulation dynamic recrystallization rate and the simulation strain:
and obtaining a through critical mathematical model of the 06Cr19Ni9NbN steel forging by taking a derivative of the simulated strain according to the simulated dynamic recrystallization rate:
preferably, the optimal simulation parameters of the DEFORM are an ambient convection coefficient, a heat transfer coefficient with a die contact surface, a friction coefficient, a die preheating temperature, a grid number of the billet, and a grid number of the die.
Preferably, in the step (3), a finite element process simulation system DEFORMMM is adopted to simulate the environment convection coefficient of the planar strain compression process to be 0.02N/s/mm/DEG C, the heat transfer coefficient of a contact surface with a die is 3N/s/mm/DEG C, the friction coefficient is 0.7, the preheating temperature of the die is 200 ℃, the number of grids of the blank is 50000, and the number of grids of the die is 8000.
Preferably, the plane strain compression of the 06Cr19Ni9NbN steel in the step (1) is performed by a hydraulic press with a weight of 500 t;
the deformation temperature of the plane strain compression is 1000-1200 ℃, and the deformation amount of the plane strain compression is 17-46%;
and (2) measuring the actual grain size of the compressed 06Cr19Ni9NbN steel by using a Zaiss Imager metallographic microscope.
Preferably, the deformation temperature of the 06Cr19Ni9NbN steel is 1000 ℃, and the critical strain value of the 06Cr19Ni9NbN steel during full forging is 0.52;
the deformation temperature of the 06Cr19Ni9NbN steel is 1100 ℃, and the critical strain value of the 06Cr19Ni9NbN steel when being forged completely is 0.41; the deformation temperature of the 06Cr19Ni9NbN steel is 1200 ℃, and the critical strain value of the 06Cr19Ni9NbN steel during full forging is 0.35.
Compared with the prior art, the invention has the beneficial effects that:
the invention combines a plane compression experiment and finite element simulation, obtains the forging critical value of the steel aiming at the 06Cr19Ni9NbN steel thermal deformation process, establishes a forging mathematical model, and can judge the forging critical strain value of the material through macroscopic process parameters, thereby being capable of conveniently and accurately establishing the optimal forging process of the steel, saving the cost and improving the efficiency.
Drawings
FIG. 1a is a schematic diagram of a structure of a sample before compression in example 1 of the present invention, and FIG. 1b is a schematic diagram of a structure of the sample after compression;
FIG. 2 is a graph showing the relationship between rolling reduction and crystal grain size at different temperatures in example 1 and example 3 of the present invention;
FIG. 3 is a graph of reduction versus percent dynamic recrystallization at different temperatures for example 1 and example 3 of the present invention;
FIG. 4 is a graph showing the relationship between rolling reduction and elongation at different temperatures in example 2 of the present invention;
FIG. 5 is a graph showing the relationship between the rolling reduction and the yield strength at different temperatures in example 2 of the present invention;
FIG. 6 is a plot of strain versus dynamic recrystallization volume percent for example 4 of the present invention;
FIG. 7 is a graph showing the relationship between strain and dynamic recrystallization rate in example 4 of the present invention.
Detailed Description
To further illustrate the technical means and effects of the present invention adopted to achieve the predetermined objects, the following detailed description of the embodiments, technical solutions, features and effects according to the present invention will be given with preferred embodiments. The particular features, structures, or characteristics may be combined in any suitable manner in the embodiments or embodiments described below.
DEFORMMM is a finite element-based process simulation system used for analyzing various forming processes and heat treatment processes of metal forming and related industries; by simulating the entire process on a computer, engineers and designers are aided: and designing tools and product process flows, and reducing expensive field test cost. The design efficiency of the tool and the die is improved, and the production and material cost is reduced. Shorten the research and development period of new products.
Example 1
The method comprises the steps of selecting 06Cr19Ni9NbN steel as a plane strain compression experiment sample, obtaining six samples, performing a plane strain compression experiment on six 06Cr19Ni9NbN steels by using a 500t hydraulic press, wherein the reduction speed of a die is 4mm/s, the sizes of the samples are 300mm × 90mm × 55mm, the compression deformation process parameters of the six samples are shown in table 1, a schematic structure diagram of one 06Cr19Ni9NbN steel sample before and after compression is shown in fig. 1, a schematic structure diagram of other samples before and after compression is similar to that of the other samples as shown in fig. 1, quenching the six samples after the compression deformation tends to be stable, sampling the core parts of the quenched samples, grinding and polishing, performing microstructure observation (OM-optical microscope) on the six samples by using a Zaiss Imager metallographic microscope, measuring the actual average grain size according to the ASTM (average grain size) grain size measurement standard, observing a crystalline phase photograph, measuring the area of a dynamic recrystallization region where the dynamic recrystallization occurs and the area of the region where the dynamic recrystallization does not occur, calculating the actual dynamic recrystallization percentage, as shown in fig. 2, the inflection point, the relationship between the temperature and the temperature of the steel at different temperatures, the temperature, the reduction relationship between the temperature and the temperature of the steel, the temperature of the steel is shown in the temperature of the steel, the steel is respectively, the temperature of the steel is shown in the temperature, the temperature of the steel is gradually increased, the temperature of the steel is shown in the temperature of the steel is changed, the temperature of the temperature.
TABLE 1 parameters of plane strain compression experiment
Example 2
Carrying out room-temperature tensile tests on the six compressed samples in example 1 by using an electronic universal testing machine (ag-xpivs100KN), setting the tensile speeds to be 4mm/min, and measuring the actual elongation and the actual yield strength of the six compressed samples; FIG. 4 is a graph showing the relationship between the rolling reduction and the elongation at different temperatures of the steel, and FIG. 5 is a graph showing the relationship between the rolling reduction and the yield strength at different temperatures of the steel; as can be seen from fig. 4, the actual elongation of the sample after compression first increases and then becomes gentle with an increase in the reduction amount, and similarly, as can be seen from fig. 5, the actual yield strength of the sample after compression first increases and then becomes gentle with an increase in the reduction amount, and the relationship between the mechanical properties and the reduction amount (strain) indicates that the steel has been fully forged, and therefore, the actual elongation and the corresponding strain, the actual yield strength and the corresponding strain, at the time of fully forging the steel at 1000 ℃, 1100 ℃ and 1200 ℃, respectively, are obtained. The actual yield strength and actual elongation obtained by example 2 have tended to stabilize indicating that the steel has just been forged through at the corresponding temperature and the corresponding reduction.
Example 3
Simulation is carried out on the whole compression process of the embodiment 1 by using DEFORMMM software, and the deformation temperature and the deformation amount of plane strain compression adopted in the simulation are the same as the process parameters of the experiment of the embodiment 1; DEFORMM simulation parameter settings: the convection coefficient of the environment is 0.02N/s/mm/DEG C, the heat transfer coefficient of the contact surface of the mold is 3N/s/mm/DEG C, the friction coefficient is 0.7, the preheating temperature of the mold is 200 ℃, the number of grids of the blank is 50000, and the number of grids of the mold is 8000; obtaining the simulated grain size and the simulated dynamic recrystallization percentage of the sample after the 06Cr19Ni9NbN steel is compressed through simulation;
as shown in fig. 2, the reduction and the grain size of the steel under the simulated environment at different temperatures are plotted, and as shown in fig. 3, the reduction and the dynamic recrystallization percentage of the steel under the simulated environment at different temperatures are plotted;
as can be seen from FIG. 2, the variation law of the rolling reduction and the grain size actually measured in example 1 is substantially the same as the variation law of the rolling reduction and the grain size simulated in example 3; similarly, as can be seen from fig. 3, the variation law of the rolling reduction and the dynamic recrystallization fraction actually measured in example 1 is substantially the same as the variation law of the rolling reduction and the dynamic recrystallization fraction simulated in example 3, which indicates that the set simulation parameters are suitable for the simulation process and can be used as the optimal simulation parameters.
Example 4
Under the condition of the optimal simulation parameters of the DEFORM, obtaining a model expression of the simulated strain and the simulated dynamic recrystallization percentage according to the change rule of the simulated grain size and the simulated dynamic recrystallization percentage simulated by the DEFORM:
wherein, XdIs the dynamic recrystallization percentage, ε is the strain, εcFor recrystallization critical strain, ε p is the peak strain; the simulated strain versus the simulated dynamic recrystallization percentage is shown in FIG. 6;
and (3) obtaining a derivative of the simulated dynamic recrystallization percentage to the simulated strain to obtain a mathematical expression of the simulated dynamic recrystallization rate and the simulated strain:
the relationship between the simulated dynamic recrystallization rate and the simulated strain is shown in FIG. 7;
and (3) obtaining a complete critical mathematical model of the 06Cr19Ni9NbN steel forging by taking a derivative of the simulated dynamic recrystallization rate to the simulated strain:
wherein Z represents a temperature compensation strain rate factor, epsilon represents strain, and omega represents a forge through critical value; when the forging critical value omega is zero, the 06Cr19Ni9NbN steel is forged completely; as shown in FIG. 7, the strain at the inflection point is the forged critical strain value of 06Cr19Ni9NbN steel;
as shown in FIG. 7, the 06Cr19Ni9NbN steel had a deformation temperature of 1000 ℃ and a critical strain value of 0.52 at the time of full forging; the deformation temperature of 06Cr19Ni9NbN steel is 1100 ℃, and the critical strain value of the steel during full forging is 0.41; the 06Cr19Ni9NbN steel had a deformation temperature of 1200 ℃ and a critical strain value of 0.35 at the time of full forging.
The dynamic recrystallization is an important parameter for representing whether the forging is complete, the dynamic recrystallization is firstly rapidly increased and then gradually tends to be stable along with the increase of the rolling reduction, the slopes of the strain and dynamic recrystallization curves (namely the dynamic recrystallization rate) are firstly rapid and then slow, the turning point (namely the inflection point) of the change in the relation process is found, the second derivative of the dynamic recrystallization rate is solved, and the obtained inflection point is the solved strain value.
From the grain size at the inflection point of fig. 2, the dynamic recrystallization percentage at the inflection point of fig. 3, the mechanical properties at the inflection points of fig. 4 and 5 tend to be stable, and thus it can be considered that the above-mentioned 06Cr19Ni9NbN steel has been forged through at the corresponding temperature.
By comparing the results of the compression experiment in example 1 (see fig. 2 and 3), the results of the tensile experiment in example 2 (see fig. 4 and 5), and the results of the simulation experiment in example 4 (see fig. 6 and 7), all of which show that the change rule and the characteristic parameter of the 06Cr19Ni9NbN steel are substantially consistent when the steel is fully forged at the corresponding temperature, it is further verified that the optimal simulation parameter simulated in example 3 is correct, and the model for obtaining the critical strain value for full forging established in example 4 is correct. The simulation process of the invention can accurately replace the actual experiment process, and the simulation model of the invention can simulate the experiment data which is not implemented in the actual experiment.
The invention mainly aims to establish a novel forging critical model for judging whether steel is forged thoroughly, and has the advantages that the established model contains strain, temperature and strain rate, the forging critical formula can be used for conveniently calculating the forging of the steel under the condition of which parameters can be obtained, and the accuracy of a calculation result is verified through experiments. The mathematical model was first proposed in the industry and was established based on the change in the percentage of dynamic recrystallization under different deformation parameters.
In the method, according to the forging critical model established by the invention, when the forging critical value is zero according to the known forging actual temperature, the critical strain value of the 06Cr19Ni9NbN steel at the forging actual temperature can be calculated, the forging critical strain value obtained by theoretical calculation is applied to the forging process of the actual 06Cr19Ni9NbN steel, and when the measured strain of the steel reaches the critical strain value, the steel is forged thoroughly at the preset temperature. The method for judging whether the 06Cr19Ni9NbN steel is completely forged has the advantages of simple operation, accurate judgment and rational basis, improves the working efficiency and saves materials and energy.
The above disclosure is only for the specific embodiments of the present invention, but the scope of the present invention is not limited thereto, and any person skilled in the art can easily conceive of the changes or substitutions within the technical scope of the present invention, and shall be covered by the scope of the present invention. Therefore, the protection scope of the present invention shall be subject to the protection scope of the above claims.
Claims (6)
1. A method for judging the forging penetration of 06Cr19Ni9NbN steel comprises the following steps:
(1) carrying out plane strain compression on 06Cr19Ni9NbN steel, and measuring the actual grain size and the actual dynamic recrystallization percentage of the compressed 06Cr19Ni9NbN steel;
(2) simulating the 06Cr19Ni9NbN steel by using a finite element process simulation system DEFORM to perform a plane strain compression process under the condition that the compression process parameters are the same as those in the step (1), and obtaining the simulated grain size, the simulated dynamic recrystallization percentage and the change rule of the two of the compressed 06Cr19Ni9NbN steel;
(3) comparing the actual grain size with the simulated grain size, comparing the actual dynamic recrystallization percentage with the simulated dynamic recrystallization percentage, and adjusting the simulation parameters of the finite element process simulation system DEFORM to obtain the optimal simulation parameters of the DEFORM after the simulated grain size is the same as the actual grain size and the actual dynamic recrystallization percentage is the same as the simulated dynamic recrystallization percentage;
under the condition of the known optimal simulation parameters of the DEFORM, re-simulating the change rule of the simulated grain size and the simulated dynamic recrystallization percentage by using the DEFORM to obtain a forging critical model of the 06Cr19Ni9NbN steel:
wherein, omega is a forging critical value, and epsilon is strain;
z represents a temperature-compensated strain rate factor,
wherein,
for strain rate, T is temperature;
and when omega is zero, the 06Cr19Ni9NbN steel is completely forged, and the critical strain value of the 06Cr19Ni9NbN steel is completely forged according to a complete forging critical model.
2. The method for judging the forging penetration of the 06Cr19Ni9NbN steel as claimed in claim 1, wherein the specific expression process of the forging penetration critical model of the 06Cr19Ni9NbN steel is as follows:
simulating the change rule of the simulated grain size and the simulated dynamic recrystallization percentage according to DEFORM to obtain a model expression of simulated strain and simulated dynamic recrystallization percentage:
εp＝0.0056Z0.117，
wherein, XdIs the dynamic recrystallization percentage, ε is the strain, εpIs the peak strain;
and the simulation dynamic recrystallization percentage is subjected to derivative calculation on the simulation strain to obtain a mathematical expression of the simulation dynamic recrystallization rate and the simulation strain:
and obtaining a through critical mathematical model of the 06Cr19Ni9NbN steel forging by taking a derivative of the simulated strain according to the simulated dynamic recrystallization rate:
3. the method of claim 1, wherein the optimal simulation parameters of DEFORM are ambient convection coefficient, heat transfer coefficient to the die contact surface, friction coefficient, die preheating temperature, the number of dies and the number of dies.
4. The method for determining the forging penetration of the 06Cr19Ni9NbN steel according to claim 1, wherein the environmental convection coefficient of the DEFORM simulation plane strain compression process in the step (3) is 0.02N/s/mm/° C, the heat transfer coefficient of the contact surface with the die is 3N/s/mm/° C, the friction coefficient is 0.7, the die preheating temperature is 200 ℃, the number of grids of the blank is 50000, and the number of grids of the die is 8000.
5. The method for judging the full forging of the 06Cr19Ni9NbN steel as claimed in claim 1, wherein the plane strain compression of the 06Cr19Ni9NbN steel in the step (1) is performed by a hydraulic press with a weight of 500 t;
the deformation temperature of the plane strain compression is 1000-1200 ℃, and the deformation amount of the plane strain compression is 17-46%;
and (2) measuring the actual grain size of the compressed 06Cr19Ni9NbN steel by using a Zaiss Imager metallographic microscope.
6. The method for judging the full forging of 06Cr19Ni9NbN steel according to claim 1, wherein the deformation temperature of the 06Cr19Ni9NbN steel is 1000 ℃, and the critical strain value of the 06Cr19Ni9NbN steel at the full forging is 0.52; the deformation temperature of the 06Cr19Ni9NbN steel is 1100 ℃, and the critical strain value of the 06Cr19Ni9NbN steel when being forged completely is 0.41; the deformation temperature of the 06Cr19Ni9NbN steel is 1200 ℃, and the critical strain value of the 06Cr19Ni9NbN steel during full forging is 0.35.
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| CN110993040B (en) * | 2019-11-28 | 2023-03-14 | 太原科技大学 | Method for determining critical value of 30Cr2Ni4MoV steel converted from cast state to forged state |
| CN112945765A (en) * | 2019-12-11 | 2021-06-11 | 宝武特种冶金有限公司 | Titanium alloy reversing forging test method based on numerical simulation |
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