CN110705108A - Method for determining hot working temperature range of low-alloy high-strength steel for ocean engineering - Google Patents
Method for determining hot working temperature range of low-alloy high-strength steel for ocean engineering Download PDFInfo
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Abstract
A method for determining a hot working temperature interval of low-alloy high-strength steel for ocean engineering belongs to the technical field of steel processing for ocean engineering. The method comprises the steps of firstly carrying out a high-temperature compression experiment on the low alloy steel to obtain a true stress-strain curve, then establishing a high-temperature deformation constitutive equation and a thermal deformation processing diagram of the material by adopting a hyperbolic sine model, and determining a tissue evolution mechanism of different regions in the processing diagram by combining a microstructure. The thermal deformation constitutive model and the thermal processing diagram are combined, and the thermal deformation rheological stress and the thermal deformation power dissipation efficiency under any deformation condition are analyzed, so that the optimal thermal processing temperature interval is obtained, and the result has significance for controlling the thermal processing process of the alloy steel.
Description
Technical Field
The invention belongs to the technical field of steel processing in ocean engineering, and particularly relates to a method for determining a hot processing area of low-alloy high-strength steel.
Background
The steel for ocean engineering is a key material in the construction of ocean structures, and has the characteristics of high strength, high toughness, corrosion resistance and the like, so that the application of high-strength steel and corrosion-resistant steel is more and more common, and the requirement is higher and higher. The seabed wellhead and oil production equipment are important unit equipment in ocean oil and gas development engineering and are also components of a seabed oil production system. Under the severe working conditions of high pressure, low temperature, seawater and oil gas corrosion and the like on the seabed, the performance and the quality of seabed equipment play an important role in the safety of an oil well. In recent years, although China's marine petroleum equipment materials have made great progress, compared with the international level, the materials still have a plurality of gaps and defects, and the development requirements of China's marine petroleum equipment are difficult to meet. China does not have the technology and equipment for implementing deep sea oil and gas exploration and development, particularly the field of underwater oil and gas exploration and development, all key and core materials used in underwater wellhead forge pieces are imported, and domestic components have large differences from foreign countries in the aspects of performance stability and batch supply capacity. Therefore, it becomes important to select materials suitable for manufacturing forgings for subsea wellheads, design and manufacture high pressure grade forgings for deep-sea wellhead systems, and study the rheological behavior of the materials to obtain basic parameters of the materials with respect to plastic deformation.
The thermal compression process of the low-alloy steel is researched through a thermal simulation test, the rheological behavior of the alloy at different temperatures and strain rates is analyzed, and necessary experimental data and reliable theoretical basis are provided for determining the hot working production process rule of the steel.
Disclosure of Invention
The invention aims to provide a method for determining a hot working temperature interval of low-alloy high-strength steel. The method can more accurately judge the heat deformation structure evolution mechanism and the hot processing performance of the low-alloy high-strength steel under different conditions, and has important guiding significance for reasonably formulating the hot processing technology of the low-alloy high-strength steel.
In order to achieve the purpose, the technical scheme provided by the invention is as follows:
a method for determining a hot working temperature interval of low-alloying high-strength steel for ocean engineering comprises the following steps:
step 1: and performing a high-temperature compression experiment on the low-alloy high-strength steel at different deformation temperatures and strain rates to obtain true stress-strain curve data of the low-alloy high-strength steel.
Step 2: establishing a high-temperature rheological stress constitutive equation of the low-alloy high-strength steel, which is shown as the following formula:
in the formula: f (σ) is a function of stress, A is a constant independent of deformation; q is deformation activation energy (J/mol); r is a gas constant of 8.314J/(mol.K); t is the thermodynamic temperature (K); σ represents peak stress (MPa);
the stress function F (σ) has the following 3 expressions: alpha sigma<0.8 is the low stress level, F (σ) ═ σ n1；ασ>1.2 high stress level, F (σ) ═ exp (β σ); for all stress states F (σ) ═ sinh (α σ)]n(ii) a Where n is the index of the stress in the composition,
as strain rate, n1And β is a material constant, α is a stress level parameter; if alpha, A, n and Q are solved, the high-temperature rheological characteristics of the material can be described through a thermal deformation constitutive equation;
and step 3: the material thermal processing diagram established according to the dynamic material model can more intuitively reflect the deformation rule of the material at different temperatures and strain rates. Power dissipation efficiency factor eta and instability criterion for describing power dissipation characteristics of material
Can be expressed as:
wherein m is a strain rate sensitive factor, and under the same strain quantity, an eta contour map, namely a power dissipation map, is drawn on a two-dimensional plane of temperature-strain rate, and then parameters are drawnThe negative region, the hot working instability map, is combined to produce a hot working map of the material. Observing the microstructure of the low-alloy high-strength steel under different deformation conditions, and determining a rheological destabilization area, a dynamic recrystallization area and a dynamic recovery area in a hot working diagram by combining the microstructure with the hot working diagram.
And 4, step 4: and (3) combining the constitutive equation established in the step (2) and the thermal processing diagram obtained in the step (3) to study the thermal deformation behavior of the material, predicting stress-strain curves under different deformation conditions by using the established constitutive model, determining power dissipation efficiency factors under different deformation conditions corresponding to different positions in the thermal processing diagram, and further determining a thermal deformation structure evolution mechanism and a thermal processing temperature interval of the material.
The low-alloy high-strength steel comprises the following chemical components in percentage by mass: c: 0.10 to 0.80 percent; mn: 0.40 to 1.50 percent; si: 0.10 to 1.0 percent; cr: 0.50% -2.0%; mo: 0.10 to 1.0 percent; v: 0.01 to 0.5 percent; p is less than or equal to 0.005 percent; s is less than or equal to 0.005 percent; the balance being Fe;
in the step 1, the deformation temperature is 850-1200 ℃, the interval of the deformation temperature is 100 ℃, and the strain rates are respectively 0.1s-1、1s-1、10s-1The true strain amount is about 0.9.
R, n and ln [ sinh (alpha sigma)]The value of the slope of the 1/T linear relationship is substituted for equation (4), and the heat distortion activation energies Q and A in step 2 are obtained. M in step 3 can be determined by
The slope is obtained.
Advantages and advantageous effects of the invention
The method combines the thermal deformation constitutive equation and the thermal processing diagram, and utilizes the two methods of the thermal processing diagram and the constitutive equation to verify mutually, so that the thermal deformation structure evolution mechanism and the thermal processing interval under different conditions can be more accurately judged, the thermal deformation and dynamic recrystallization information of the material under certain deformation conditions can be obtained, and important reference is provided for the thermal processing process of the material.
Drawings
Figure 1 is a thermal compression true stress-strain curve under different deformation conditions,
FIG. 2 shows the strain rate of 0.1s-1A microstructure compressed at different deformation temperatures, (a)850 ℃; (b)950 ℃; (c)1050 ℃; (d)1150 ℃.
FIG. 3 is a hot working drawing, (a) true strain is 0.6; (b) the true strain was 0.8.
Detailed Description
For a further understanding of the invention, reference will now be made to the following detailed description taken in conjunction with the accompanying drawings.
Example 1
A method for determining a hot working temperature interval of low-alloy high-strength steel for ocean engineering.
The low-alloy high-strength steel comprises the following chemical components in percentage by mass: c: 0.37 percent; mn: 0.84 percent; si: 0.22 percent; cr: 0.95 percent; mo: 0.2 percent; v: 0.033%; p: 0.008 percent; s: 0.0028%; the balance being Fe.
The method comprises the following steps:
step 1: the deformation temperature is 850-1200 ℃, the interval of the deformation temperature is 100 ℃, and the strain rates are respectively 0.1s-1、1s-1、10s-1And performing a high temperature compression test on the low alloy steel under a thermal deformation condition with a true strain amount of 0.9 to obtain a true stress-strain curve of the low alloy high strength steel, as shown in fig. 1, wherein
As can be seen from the graph, at the same strain rate, the peak stress gradually decreases as the deformation temperature increases, and at the same deformation temperature, the peak stress gradually increases as the strain rate increases. In the initial stage of deformation, the stress rises rapidly with the increase of strain, mainly because the sample is fully recrystallized after a period of high-temperature heat preservation, and the dislocation is multiplied after the sample is compressed and deformed to cause work hardening. As the amount of sample deformation increases, the grain internal dislocations recombine through interaction. Along with the further increase of the strain of the sample, the dislocation density is increased, dynamic recrystallization is excited, and the stress gradually decreases after reaching the peak value. During the subsequent deformation, the softening effect produced by the dynamic recrystallization and the work hardening effect produced by the strain increase cancel each other out, and the deformation enters a steady-state phase. It can also be seen from FIG. 1 that at temperatures of 1000 ℃ and below (e.g., 950 ℃), the strain rate is low (e.g., 0.1 s)-1) As the amount of deformation increases, the rheological stress continues to increase to peak stress. At 1050 deg.C or aboveWhen the temperature is deformed, the rheological stress is increased along with the increase of the deformation amount, and the softening phenomenon is more obvious after the peak value is reached. And the higher the deformation temperature and the lower the strain rate, the more pronounced the softening effect, i.e. the more pronounced the dynamic recrystallization behavior, which occurs.
Step 2: establishing a high-temperature rheological stress constitutive equation of the low-alloy steel, which is shown as the following formula:
in the formula: f σ) is a function of stress, where a is a constant independent of deformation; q is deformation activation energy (J/mol); r is a gas constant of 8.314J/(mol.K); t is the thermodynamic temperature (K); σ represents peak stress (MPa);
the stress function F (σ) has the following 3 expressions: at low stress levels (α σ)<0.8)F(σ)＝σ n1; at high stress levels (α σ)>1.2) F (σ) ═ exp (β σ); for all stress states F (σ) ═ sinh (α σ)]n(ii) a Where n is the index of the stress in the composition,
as strain rate, n1And β is a material constant, α is a stress level parameter; wherein α ═ β/n1Is obtained by1And beta are each independentlyAnd
the average of the inverse of the slope of the straight line is obtained by linear regression, and finally the value of beta is 0.0868, n19.682, α is 0.0896 after solving. n is
The inverse slope of the linear relationship 5.884. Then, the 1/T is subjected to partial derivation by the formula (1)
R, n and ln [ sinh (alpha sigma)]Substituting the value of the slope of the 1/T linear relationship into formula (4) to obtain the thermal deformation activation energy Q-427.469 kJ/mol and A-e26.43. Finally, the thermal deformation constitutive equation of the low alloy steel is obtained as follows:
FIG. 2 shows a strain rate of 0.1s-1The structure and appearance of the low-alloy high-strength steel after compression at different temperatures. As can be seen from fig. 2(a) and (b), different degrees of recrystallization occurred upon compression at 850 and 950 ℃, with a small number of elongated recrystallized grains. And the sample produced a band of significant distortion, indicating that the grains were elongated during compression. FIG. 2(c) shows a deformed structure at 1050 ℃ compression, and it can be seen that a recrystallization process occurs and the crystal grains are fine. While the grains are seen to grow significantly when compressed at 1150 c in fig. 2(d), dynamic recrystallization is more likely to occur due to the higher temperature, the higher the thermal activation energy of the atoms, the greater the driving force for element diffusion, dislocation glide and migration, and grain boundary migration.
And step 3: the material thermal processing diagram established according to the dynamic material model can more intuitively reflect the deformation rule of the material at different temperatures and strain rates. Power dissipation efficiency factor eta and instability criterion for describing power dissipation characteristics of material
Can be expressed as:
where m is the strain rate sensitive factor, can be determined by
The slope is obtained. Drawing a contour map of eta, namely a power dissipation map, on a two-dimensional plane of temperature-strain rate under the same strain quantity, and then drawing parameters
The negative region, the hot working instability map, is combined to obtain the hot working map of the material. As shown in fig. 3, the hot working patterns of the low alloy steel at true strain amounts of 0.6 and 0.8 are shown, respectively. The shaded area in the energy consumption diagram is the rheological destabilization area, where the deformation efficiency values are low. The other regions represent deformation stabilization zones. Deformation in the destabilization region should be avoided during subsequent processing.
The hot working pattern when the strain amount is 0.6 is shown in FIG. 3(a), and the strain rate is 2.33 to 10s-1In the temperature range of 1100-1200 ℃, the steel is in a destabilization area of hot working deformation. At higher strain rates, the material is more susceptible to slippage at the grain or phase interface, resulting in severe stress concentrations at the interface, which can cause interfacial cracking. When the strain rate is lower than 2.33s-1In the whole range of 850-1200 ℃, the steel is in a safe zone of hot working deformation.
When the strain amount is 0.8, the thermal processing diagram is shown in FIG. 3(b), the instability region is mainly distributed below 900 ℃, and the strain rate is 0.1-10 s-1And the temperature is 1050-1150 ℃, and the strain rate is 3-10 s-1To (3). The reason is mainly that the material is severely deformed and the dislocation is sharply increased along with the increase of the strain amount, so that a large number of defects are formed. At lower temperatures and higher strain rates, increased dislocation density tends to form stress concentrations that result in micro-domain cracking leading to failure. Therefore, the optimum hot working deformation condition range of the low alloy steel is determined as follows: the temperature is 950-1100 ℃, and the strain rate is 0.1-1 s-1。
The method for determining the hot working temperature interval of the low-alloy high-strength steel combines a thermal deformation constitutive equation and a hot working diagram, and utilizes two methods of a processing diagram and the constitutive equation to verify mutually, so that the evolution mechanism and the hot working performance of a thermal deformation structure under different conditions can be more accurately judged, thermal deformation and dynamic recrystallization information of a material under a certain deformation condition is obtained, and important reference is provided for the hot working process of the material.
Claims (4)
1. A method for determining a hot working temperature range of low-alloy high-strength steel for ocean engineering is characterized by comprising the following steps:
step 1: performing a high-temperature compression experiment on the low-alloy high-strength steel at different deformation temperatures and strain rates to obtain true stress-strain curve data of the low-alloy high-strength steel;
step 2: establishing a high-temperature rheological stress constitutive equation of the low-alloy high-strength steel, which is shown as the following formula:
in the formula: f (σ) is a function of stress, A is a constant independent of deformation; q is deformation activation energy (J/mol); r is a gas constant of 8.314J/(mol.K); t is the thermodynamic temperature (K); σ represents peak stress (MPa);
the stress function F (σ) has the following 3 expressions: alpha sigma<At 0.8, a low stress level,ασ>1.2, high stress level, F (σ) ═ exp (β σ); for all stress states F (σ) ═ sinh (α σ)]n(ii) a Where n is the index of the stress in the composition,
as strain rate, n1And β is a material constant, α is a stress level parameter; if alpha, A, n and Q are solved, the high-temperature rheological characteristics of the material can be described through a thermal deformation constitutive equation;
and step 3: the material thermal processing diagram established according to the dynamic material model can more intuitively reflect the deformation rule of the material at different temperatures and strain rates; describing material power consumptionPower dissipation efficiency factor eta of dispersion characteristics and instability criterion
Expressed as:
wherein m is a strain rate sensitive factor, and under the same strain quantity, an eta contour map, namely a power dissipation map, is drawn on a two-dimensional plane of temperature-strain rate, and then parameters are drawn
A negative area, namely a hot working instability image, and the two are combined together to obtain a hot working image of the material; observing the microstructure of the low-alloy high-strength steel under different deformation conditions, and determining a rheological destabilization area, a dynamic recrystallization area and a dynamic recovery area in a hot working diagram by combining the microstructure with the hot working diagram;
and 4, step 4: and (3) combining the constitutive equation established in the step (2) and the thermal processing diagram obtained in the step (3) to study the thermal deformation behavior of the material, predicting stress-strain curves under different deformation conditions by using the established constitutive model, determining power dissipation efficiency factors under different deformation conditions corresponding to different positions in the thermal processing diagram, and further determining a thermal deformation structure evolution mechanism and a thermal processing temperature interval of the material.
2. The method for determining the hot working temperature interval of the low-alloy high-strength steel for the ocean engineering according to claim 1, wherein the low-alloy high-strength steel comprises the following chemical components in percentage by mass: c: 0.10 to 0.80 percent; mn: 0.40 to 1.50 percent; si: 0.10 to 1.0 percent; cr: 0.50% -2.0%; mo: 0.10 to 1.0 percent; v: 0.01 to 0.5 percent; p is less than or equal to 0.005 percent; s is less than or equal to 0.005 percent; the balance being Fe.
3. The method for determining the hot working temperature interval of the low-alloy high-strength steel for ocean engineering according to claim 1, wherein the method comprises the following steps: in the step 1, the deformation temperature is 850-1200 ℃, the interval of the deformation temperature is 100 ℃, and the strain rates are respectively 0.1s-1、1s-1、10s-1The true strain amount was 0.9.
4. The method for determining the evolution mechanism and the hot working performance of the hot deformed structure of the low-alloy high-strength steel as claimed in claim 1, wherein: in step 2, alpha is beta/n1And n is1And beta are each independently
And
the average of the inverse of the slope of the straight line is calculated according to linear regression; n in step 2 isThe inverse slope of the linear relationship; by the formula (1) to obtain the partial derivative of 1/T
R, n and ln [ sinh (alpha sigma)]-the value of the slope of the 1/T linear relationship is substituted for formula (4) to obtain the thermal deformation activation energies Q and A in step 2; m in step 3 byThe slope is obtained.
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