ISSN:2321-6212

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^{1}School of Mechanical Engineering and Automation, University of Science and Technology Liaoning,
Anshan 114051, China

^{2}College of Mechanical & Electrical Engineering, Shaanxi University of Science & Technology, Xi’an
710021, China

^{3}School of Materials Science & Engineering, Northwestern Polytechnical University Xi’an 710072, China

- *Corresponding Author:
- LIU Yan-hui

College of Mechanical & Electrical Engineering

Shaanxi University of Science& Technology

Xi’an 710021, China

**Tel:**+86-29-88493744

**Fax:**+86-29-88492642

**E-mail:**[email protected]

**Received Date**: 13/09/2017; **Accepted Date:** 03/10/2017; **Published Date**: 12/10/2017

DOI: 10.4172/2321-6212.1000197

**Visit for more related articles at** Research & Reviews: Journal of Material Sciences

In order to optimize the hot working technology of powder metallurgy high speed steel, The hot deformation behavior of powder metallurgy (PM) high speed steel was investigated by Gleeble-1500D simulation at the temperature range of 1000-1150°C, strain rates between 0.001 s-1 and 1.0 s-1 and deformation rate of 60% of the samples. The flow stress under different temperatures and strain rates were analyzed. The results show that the flow stress is influenced strikingly by deformation temperature and strain rate. Both the peak stress and the corresponding strain decrease with the increase of temperature and the decrease of strain rate. Deformation temperature, strain rate and deformation activation energy have a great affect on the microstructure. The value of deformation activation energy is 750.67 kJ/mol. The mathematical model of the strain corresponding to the peak stress was set up. The relationship between the strain corresponding to the peak stress and the strain corresponding to the critical stress can be described as: εc=0.606 εp. The segmental dynamic constitutive equation under different strain was established based on the idea of subsection.

The high-speed steel is a kind of steel with special performance, it has good performance and excellent combination of stable hardness and good toughness [1,2]. It is used mostly to manufacture complex thin blade and metal cutting tool, also can be produced high temperature bearing and cold extrusion mould. However, this alloy is rather difficult to deform because of a high content of alloy elements. Its hot workability is sensitive to deformation temperature and strain rate. With the development of the industry, the powder metallurgy (PM) high-speed steel came next. The PM high-speed steel has the advantage of avoiding the mechanical properties degradation and heat treatment deformation caused by alloy elements and carbide segregation.

The hot deformation behaviors and constitutive equation for traditional high-speed steel have been studied [3,4]. But, the PM high-speed steel is relatively less investigated. In the deformation process, constitutive equation as an important part of hot deformation has been researched in a great number of steels and alloys [5-16]. Constitutive equation can be used to describe the relationship of deformation temperature, true strain, strain rate and flow stress. However, the dynamic softening mechanism has a great effect on the flow stress. When building the constitutive equation, the dynamic softening mechanism should be thought about. In this paper, in order to describe dynamic recrystallization, a new dynamic constitutive equation was put forward to study this PM high-speed steel. Based on the thermal simulation of compression under different deformation temperatures and strain rates, we preliminarily studied the peak stress and the corresponding strain, the critical stress and the corresponding strain, and finally established the new dynamic constitutive equation. All of them are benefit for the hot deformation study of the PM highspeed steel.

The high-speed steel used in this investigation was produced by hot isostatic press (HIP). The original powder particles are
procured by argon atomization, and its diameter range from 20 to 50 μm. The chemical composition (wt,%) is: C, 1.15; Cr, 4.00;
V, 3.00; W, 6.00; Mo, 5.00; Fe to balance. The powder was encapsulated in a stainless steel capsule, and then produced by HIP
at the temperature of 1100-1150°C and the pressure of 110 MPa for 3 hours. **Figure 1** presents the typical microstructure of
this PM high-speed steel before hot deformation consisting of a tempered martensite matrix with fine and uniformly distributed
carbides.

The cylindrical compression specimens of 8 mm in diameter and 12 mm in height were machined from the as-HIPed
billet. Isothermal hot compression tests were conducted on a Gleeble-1500D thermo-simulation machine under the deformation
temperatures of 1000, 1050, 1100 and 1150°C, and the constant strain rates were selected as 0.001, 0.01, 0.1 and 1.0 s^{-1},
respectively. All compression specimens were heated with a rate of 10°C/s and maintained for 3 minutes. The specimens were
compressed by 60% of the original height followed by the spray quenching for microstructural observation. The whole processes
of heating, heat preservation and hot compression were protected by the argon. After deformation, the grain structures of the
deformed specimens were observed by an OLYMPUS-PMG3 optical microscope to analyze the microstructure.

**Flow Stress Behavior**

**Figure 2** shows typical true stress-true strain curves of this PM high-speed steel under different deformation temperatures
and strain rates. These curves can be used to show the effect of deformation temperature, strain rate and true strain on the flow
stress. Most of the curves exhibited typical characteristics of dynamic recrystallization (DRX) [17]. The flow stress firstly increased
to a peak value because of work hardening with the increase of true strain, then decreased and gradually turned to be stable
later on. The peak stress appears at the strains range of 0.05-0.10. The strains corresponding to the peak stress increases
with the decrease of temperature and the increase of strain rate. Consequently, DRX acts as the main softening mechanism.
However, the decrease of temperature and the increase of strain rate will delay the onset of DRX. After the peak stress, the
stress decreases with the increase of strain. Under certain conditions, a steady stress state is achieved in which the flow stress
remains nearly constant with the increase of strain. Such a flow behavior indicates that the effect of softening mechanisms (DRX,
DRV) is sufficiently enough to cancel out the effect of work hardening. This has a good agreement with the observations of other
materials, such as super-alloys [18] and titanium alloys [19].

**The Relationship of the Peak Stress and the Corresponding Strain**

Based on the true stress-true strain curves of this PM high-speed steel, the peak stress and the corresponding strain can
be got. The peak stress and the corresponding strain under different deformation temperatures and strain rates are shown in **Figures 3 and 4**. Based on the experimental results, deformation temperature and strain rate have a great effect on the peak
stress and the corresponding strain. Both of them increase with the decrease of temperature and the increase of strain rate.
There are two reasons that account for this phenomenon. On the one hand, with the increase of deformation temperature,
the thermal activation of material increases, the average kinetic energy of atoms increases, and the critical cutting stress of
crystal slip reduces, the blocking effect between the dislocation motion and slip reduces. On the other hand, with the increase of
deformation temperature, dynamic softening is more likely to happen. It can reduce the dislocation density and offset the work
hardening in the deformation process, thus promote the peak stress and the corresponding strain decrease [20]. Therefore, with
the increase of deformation temperature, the peak stress and the corresponding strain decrease gradually. Under a low strain
rate, the plastic deformation per unit time is reduced, and there is plenty of time for creep deformation. The reducing of the rate
of dislocation proliferation leads to the decrease of dislocation density. The deformation twin, dislocations and other defects
decrease in the process of deformation, they will lead to the decreases of the flow stress. At the same time, the extension of the
deformation time is benefit for the fully DRX, and it leads to the decrease of the peak stress and the corresponding strain.

According to Sellers [17,18], the relationship among the strain corresponding to the peak stress ε_{p}, the deformation temperature
T and the strain rate ε could be expressed as follows:

ε = a_{2} ε^{.m1} exp(Q_{1} / RT) (1)

Where, Q_{1} is the recrystal activation energy; R is the gas constant; and m_{1} and a_{2} are the constants.

The relationship among the strains corresponding to the peak stress and the critical stress could be expressed as follows:

(2)

Where, εc is the strains corresponding to the critical stress, a_{1} is the constant.

According to the linear regression of the experimental data, it can be obtained that Q_{1}=86.09 KJ/mol, a_{2}=2.02 × 10^{-5} and
m_{1}=0.08795. Therefore, under the deformation conditions of the temperature range of 1000-1150°C, strain rates between
0.001 s^{-1} and 1.0 s^{-1}, the strain corresponding to the peak stress can be expressed as follows:

(3)

The strain corresponding to the peak stress between simulation and experiment is shown in **Figure 5**, the error between the calculated value and experimental value is small, and the average value of error is less than 4%. Therefore, this established
mathematical model can be used to calculate the strain corresponding to the peak stress under different temperature and
different strain rate.

**The Activation Energy for Hot Deformation**

According to Sellers [21,22], the relationship among the flow stress, the deformation temperature and the strain rate could be expressed by a universal hyperbolic sine function as follows:

(4)

Where, σ is the flow stress; Q is the hot deformation activation energy; A, а and n are the constants.

Zener-Hollomon parameter (Z parameter), known as temperature modified strain rate, was widely used to characterize the combined effect of strain rate and temperature on the deformation process. It can be expressed in the following equation:

(5)

The logarithm of eqn. (4) can be expressed by:

ln ε = ln A + nln[sinh(ασ )] − Q/ RT (6)

Taking partial derivative of both sides of eqn. (6) to strain rate and 1/T, the hot deformation activation energy can be expressed by:

(7)

Based on the eqn. (7), the hot deformation activation energy Q can be obtained. **Table 1** shows the Q values at different
deformation temperatures and strain rates. The results showed that the hot deformation activation energy is greatly affected by
deformation temperature and strain rate. The average value of Q is 750.673 KJ/mol under different deformation conditions.

Temperature/°C | ||||
---|---|---|---|---|

0.001 | 0.01 | 0.1 | 1 | |

1000 | 742.337 | 772.156 | 846.141 | 899.435 |

1050 | 703.621 | 731.884 | 802.011 | 852.525 |

1100 | 660.401 | 686.929 | 752.748 | 800.159 |

1150 | 621.872 | 646.852 | 708.831 | 753.476 |

**Table 1. **The values of hot deformation activation energy** ***Q*** **at different temperatures and** **strain rates.

Besides, the intrinsic relationship between the deformation activation energy and the thermal-dynamic behavior has been
studied. The value of deformation activation energy has a great effect on the microstructure. There is a great difference among
the microstructures at different deformation temperatures and strain rates. **Figure 6** shows typical deformation microstructures
of this PM high speed steel under different deformation temperatures and strain rates. At the same deformation temperature, the
deformation activation energy increases with the rising strain rate. Because of the high speed deformation and high deformation
activation energy, the dynamical recovery and the dynamical recrystallization are difficult to happen, and the shot residence
time under high temperature go against these softening mechanism, **Figure 6b and 6c** can be used to show this phenomenon
in the hot deformation. At the same strain rate, the deformation activation energy decreases with the raising deformation
temperature. Besides, the high temperature is beneficial for the dynamical recovery and the dynamical recrystallization. Based
on the microstructures, the temperature increase is beneficial for the dynamical recovery and the dynamical recrystallization, as
shown in **Figure 6c and 6d**. The continual dynamical recrystallization and grain growth would take place at a high deformation
temperature and a low strain rate, as shown in **Figure 6f**. In a word, the crushing grains take place fully dynamic recrystallization
with the increases of deformation temperature and the decreases of strain rate. As a result, the microstructure is fine and uniform.

**The Relationship of the Strain Corresponding to the Peak Stress and the Strain Corresponding to the Critical Stress**

The relationship between the strain corresponding to the peak stress and the strain corresponding to the critical stress can
be expressed as eqn. (2), the constant of a_{1} can be calculated based on the strain corresponding to the peak stress and the strain
corresponding to the critical stress at different temperatures and strain rates.

The strain hardening rate at different temperatures and strain rates can be got based on the true stress-true strain curves.
The relationship of work hardening rate with strain was obtained by fitting the linear. The strain hardening rate at temperature of
1100°C and strain rate of 0.01 s^{-1} is shown in **Figure 7**. Based on this way, the strain hardening rate at temperature of 1100°C
and different strain rates is shown in **Figure 8**. The strain hardening rate at strain rate of 0.01 s^{-1} and different temperatures is
shown in **Figure 9**.

Based on the work hardening rate curve, the strain corresponding to the critical stress under different temperatures
and strain rates can be got (shown in **Table 2**), the strain corresponding to the critical stress decreased with the increase of
temperature and the decrease of strain rate. Because, with the increase of deformation temperature and the decrease of strain
rate, the mobility of grain boundary increases, and the time of accumulation of distortion energy and dislocation annihilation will
delay, which is advantageous to softening mechanism such as the dynamic recrystallization [23].

Temperature/°C | ||||
---|---|---|---|---|

0.001 | 0.01 | 0.1 | 1 | |

1000 | 0.0229 | 0.0258 | 0.0326 | 0.0447 |

1050 | 0.0169 | 0.0208 | 0.0251 | 0.0321 |

1100 | 0.0115 | 0.0183 | 0.0197 | 0.0273 |

1150 | 0.0102 | 0.0125 | 0.0135 | 0.0204 |

**Table 2. **The strain corresponding to the critical stress of powder metallurgy high speed** **steel at different temperatures and strain rates.

According to the value of the strain corresponding to the peak stress and the strain corresponding to the critical stress, both
of them can be fitted by linear (shown in **Figure 10**), the slop of linear is 0.606, eqn. (1) can be written as:

(8)

Because the experimental materials is powder metallurgy high speed steel, the grain is small, it is easy for the dynamic
recrystallization in the process of thermal simulation of compression, and the strain corresponding to the critical stress is small,
the value of a_{1} is not big.

**Dynamic Recrystallization Constitutive Equation in Different Section**

According to the true stress-true strain curves of this PM high speed steel, the dynamic softening mechanism are dynamic recovery and dynamic recrystallization, and the two mechanisms play different leading roles in the different strain range. When the strain reaches a certain value (the critical strain), the stress has a downward trend after reaching a peak stress, the dynamic recrystallization makes a leading role at this time. The dynamic softening mechanism should be fully considered when building a constitutive equation. The dynamic recrystallization constitutive equation in different sectionals can be built, and it is better for predicting the true stress-true strain curves of the PM high speed steel under the different temperatures and strain rates. When the thermal deformation is given priority to with work hardening and dynamic recovery, the relationship between stress and strain can be expressed as [24]:

(9)

Where, C is a constant.

The logarithm of the eqn. (4) can be shown by a linear relationship, the slope of the linear is the constant C in the eqn. (9). We can choose a number of points on the true stress-true strain curves and fitting these data by using a linear:

c = 0.8739 (10)

The peak stress in the eqn. (4) can be expressed by hot deformation equation:

(11)

The eqn. (2) can be expressed by another form:

Z = εexp(Q/ RT) = A[sinh(ασ)]^{n } (12)

Using eqn. (12) in eqn. (6):

(13)

Carrying on linear regression analysis of the peak stresses under different temperatures and strain rates, the value of n,
Q and A is determined respectively as n=8.192, Q=750.673 KJ/mol, A=9.6737 × 10^{9}. So the peak stress can be expressed as:

(14)

Another expression is:

The eqn. (3) can be expressed by another form:

(15)

When the ε<ε_{p}, the piecewise constitutive equation can be expressed as:

(16)

When the ε ≥ p, based on the dynamic recrystallization mechanism, the flow stress after the occurrence of dynamic recrystallization can be described using Arrhenius equation, the piecewise constitutive equation can be expressed as:

(17)

Where, σ_{ss} is the steady state stress for dynamic recrystallization, C_{1} is a coefficient which is associated with the degree of
softening and the true stress-true strain curves.

Any point on the true stress-true strain curves before the steady state flow stress can be picked, the strain is εk and the
corresponding stress is σ_{k} (σ_{ss}<σ_{k}<σ_{p} ), the coefficient C_{1} can be got by putting the strain and the stress into the eqn. (17):

(18)

In the process of calculation, the value of εk is 0.6, and the corresponding stress σ_{k} can be determined. Putting the εk and
the σ_{k} into the eqn. (18), the values of C_{1} under every temperature and strain rate can be obtained. In addition, in the process of
selecting the value of εk, the value of C_{1} is more appropriate when the value of εk is bigger. In the process of calculation, we select
the value of εk is near 0.6 in this paper.

It is same as the calculation method of peak stress, the steady state of stress under different temperatures and strain rates can be expressed by hot deformation equation:

(19)

By regression, the value of n is determined as n=5.1027, and the value of corresponding activation energy for the steady state stress is determined as Q=466.361 kJ/mol. The value of A depends on the temperature and the strain rate, the value of A under different conditions can be obtained by regression. So the eqn. (14) can be written as:

(20)

The value of steady stress under a certain temperature and strain rate can be calculated by the above formula. Using eqns.
(14), (15) and (20) and C_{1} in eqn. (17), the constitutive equation can be obtained when ε ≥ ε_{p}.

(21)

Validation of the experimental model: the flow stresses under different temperature and strain rate can be obtained by the
above sectional constitutive equation. Taking the strain rate of 0.01 s–1 for example, the comparison between the calculated
values and experimental values can be obtained. The result is shown in **Figure 11**.

By the validation, the dynamic recrystallization constitutive equation with subsection coincide well with the experimental value, the average error is about 3.4%, especially under high temperature, the calculated flow stresses are more coincident with the results of experiments. Under a same deformation temperature, the values of error decrease gradually with the increase of the strain. The experimental value and calculated value is almost consistent after the strain reaches a certain value. Therefore, the dynamic recrystallization constitutive equation got in this paper can be used to predict the flow stress very well under the high strain.

1. The flow stress of this PM high-speed steel is influenced by strain during hot deformation. Because work hardening makes a main role in the initial stage (ε<0.1), the flow stress increases sharply and reaches peak quickly; The effect of dynamic softening is greater than the effect of work hardening with the continued increase of strain, and the flow stress gradually decreases, the flow stress tends to be stable with the further increase of strain. The flow stress decreases with increase of the deformation temperature or decrease of the strain rate.

2. The peak flow stress and the corresponding strain are strikingly influenced by deformation temperature and strain rate during hot deformation. Both of them decrease with increase of the deformation temperature or decrease of the strain rate. The mathematical model of the strain corresponding to the peak stress under different strain rate and deformation temperature is established as:

3. The strain hardening rate is extremely different in different deformation stages in the process of deformation. The
strain hardening rate decreases sharply in the initial stage of deformation. When the strain reaches the critical strain, the speed
of strain hardening rate reduction is slow, and the strain hardening rate reaches a negative value. The strain hardening rate
increases gradually and gradually tends to zero with the further increase of strain, so the flow stress reaches a steady state.
The relationship between the strain corresponding to the peak stress and the strain corresponding to the critical stress can be
described as: εc=0.606 ε_{p}.

4. The softening mechanism of dynamic recrystallization should be considered in the hot deformation, and the dynamic recrystallization constitutive equation in different sectional for the PM high speed steel are established as:

When ε<ε_{p}:

When ε ≥ ε_{p}:

The work was supported by Natural Science Foundation of China (Grant No. 51775440), the National Natural Foundation of China (Grant No. 51175431) and China Postdoctoral Science Foundation (Grant No. 2012T50818).

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