CN115029643B - Automobile part with excellent thermal shock resistance and preparation method thereof - Google Patents
Automobile part with excellent thermal shock resistance and preparation method thereof Download PDFInfo
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Classifications
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/10—Ferrous alloys, e.g. steel alloys containing cobalt
- C22C38/105—Ferrous alloys, e.g. steel alloys containing cobalt containing Co and Ni
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F1/00—Metallic powder; Treatment of metallic powder, e.g. to facilitate working or to improve properties
- B22F1/10—Metallic powder containing lubricating or binding agents; Metallic powder containing organic material
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
- B22F3/02—Compacting only
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
- B22F3/02—Compacting only
- B22F3/04—Compacting only by applying fluid pressure, e.g. by cold isostatic pressing [CIP]
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
- B22F3/10—Sintering only
- B22F3/1017—Multiple heating or additional steps
- B22F3/1021—Removal of binder or filler
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
- B22F3/10—Sintering only
- B22F3/1017—Multiple heating or additional steps
- B22F3/1028—Controlled cooling
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
- B22F3/22—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces for producing castings from a slip
- B22F3/225—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces for producing castings from a slip by injection molding
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
- B22F3/24—After-treatment of workpieces or articles
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/001—Heat treatment of ferrous alloys containing Ni
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/007—Heat treatment of ferrous alloys containing Co
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C33/00—Making ferrous alloys
- C22C33/02—Making ferrous alloys by powder metallurgy
- C22C33/0257—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements
- C22C33/0278—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements with at least one alloying element having a minimum content above 5%
- C22C33/0285—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements with at least one alloying element having a minimum content above 5% with Cr, Co, or Ni having a minimum content higher than 5%
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
- B22F3/24—After-treatment of workpieces or articles
- B22F2003/248—Thermal after-treatment
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/001—Austenite
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/004—Dispersions; Precipitations
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/008—Martensite
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Manufacturing & Machinery (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Fluid Mechanics (AREA)
- Powder Metallurgy (AREA)
Abstract
The invention discloses an automobile part with excellent thermal shock resistance and a preparation method thereof, wherein a microstructure with finer matrix grains, nanometer second phase, low impurity content and proper porosity is prepared by adopting the synergistic effect of powder metallurgy and heat treatment technology, the preparation technology of the automobile part with excellent thermal shock resistance is broken through, the thermal shock resistance of the alloy is greatly improved, the process is simple, the cost is low, the mass production is easy, and the requirements of the automobile part can be well met.
Description
Technical Field
The invention relates to an automobile part and a preparation method thereof, in particular to an automobile part with excellent thermal shock resistance and a preparation method thereof, and belongs to the technical field of automobile part processing.
Background
With the development of the automobile industry, the automobile yield in China steadily increases, the automobile consumption scale is getting huge, and higher requirements are also put forward on the performance of core component materials in automobile engines, gearboxes and brake systems. For example, the turbine is a core component for realizing pressurization, airflow can generate excitation after entering the turbine shell, the temperature in the turbine shell is higher, the long-term use temperature exceeds 500 ℃, the instantaneous working temperature can reach more than 800 ℃, and turbine blades are easy to break or deform. On the one hand, the automobile brake friction material is required to have high and stable braking force, and on the other hand, the automobile brake friction material is required to have good wear resistance so as to ensure long service life and braking stability, and the automobile brake friction material also has higher requirements on the thermal shock resistance of parts.
Thermal shock resistance refers to the ability of materials and their articles to withstand drastic changes in temperature without damage or destruction. When the material and its products are subjected to temperature drastic change to cause internal temperature gradient, thermal stress can be generated in the material due to shrinkage or expansion resistance, and when the thermal stress exceeds the strength limit of the material, phenomena such as cracking, damage, mechanical strength reduction and the like can be generated. Therefore, the quality of the thermal shock resistance of the material directly influences the safety and the efficiency of the automobile, and is also the most important performance index for evaluating the automobile parts.
The thermal shock resistance of a material is related to the mechanical strength, elastic modulus, thermal expansion coefficient, thermal conductivity, bulk density and the like of the material, and more importantly, the microstructure such as grain size, phase composition, impurity defects and the like of the material are influenced. And the chemical composition of the material, the heat treatment process and the heat processing history determine its microstructure. At present, researchers have conducted a great deal of research work on improving the thermal shock resistance of automobile parts, mainly focusing on the use of coatings. Cai Jie of Jiangsu university provides a high performance thermal barrier coating for heavy duty gas turbine blades and a method for preparing the same in combination with multiple processes. The YSZ ceramic layer is prepared by adopting a Laser Cladding (LC) technology to prepare an MCrAlY bonding layer, a laser impact composite strengthening technology to regulate and control a bonding layer tissue structure and an APS technology, and the TBCs system has excellent interface bonding strength, higher high-temperature oxidation resistance and thermal shock resistance, and solves the requirements of a gas turbine thermal barrier coating on high heat insulation, oxidation resistance, long service life and large-area controllable preparation (CN 111593341A). Zhu Shenglong of the national academy of sciences metal institute provides a high temperature protective coating material suitable for single crystal nickel-based superalloy blades. The coating prepared by the high-temperature protective coating material is suitable for single crystal nickel-based superalloy blades, has high-temperature oxidation resistance equivalent to that of a NiPtAl coating, can obviously slow down the inter-diffusion behavior of elements between the coating and a matrix, and avoids the formation of a secondary reaction zone (CN 110396623A) in the single crystal matrix, which damages the mechanical properties. The problems of high preparation difficulty, complex process, adverse effect on technological production and the like exist in the technologies. Meanwhile, no report on the influence of the alloy microstructure on the thermal shock resistance exists in the prior art so far.
Disclosure of Invention
In order to improve the thermal shock resistance of the automobile part by controlling the microstructure of the alloy, the invention provides the automobile part with excellent thermal shock resistance and a preparation method thereof, and the automobile part with excellent thermal shock resistance, which has finer matrix grains, nanometer second phase, low impurity content and proper porosity, is prepared by adopting the powder metallurgy and heat treatment technology. In order to achieve the above purpose, the present invention adopts the following technical scheme:
the invention relates to an automobile part with excellent thermal shock resistance, which is characterized by comprising the following chemical components: co: 8-15 wt.%, ni: 13-20wt.% Mo: 5-10 wt.% of Al: 0-5 wt.% Ti: 0-5 wt.% of Fe and the balance of unavoidable impurity elements, wherein the total amount of the impurity elements is less than or equal to 0.3wt.%;
the microstructure includes a matrix and a second phase;
the matrix is any one of martensite and austenite;
the grain size of the matrix is 30-50 um;
the second phase is distributed in the matrix;
the chemical composition of the second phase is Ni 3 Mo、Fe 2 Mo、Ni 3 At least one of Ti;
the particle size of the second phase is 50-200 nm;
the relative density of the automobile part is 93% -97%.
As a preferable scheme, the automobile part with excellent thermal shock resistance is characterized in that: the impurity element contains at least one of C, O, N, P, S, si and Mn in mass percent; wherein the content of C is less than or equal to 0.03 wt%, the content of O is less than or equal to 0.01 wt%, the content of N is less than or equal to 0.02 wt%, the content of P is less than or equal to 0.04 wt%, the content of S is less than or equal to 0.04 wt%, the content of Si is less than or equal to 0.1 wt% and the content of Mn is less than or equal to 0.05 wt%.
The invention relates to a preparation method of an automobile part with excellent thermal shock resistance, which is characterized by comprising the following steps of: the method comprises the steps of sequentially carrying out pretreatment, forming, sintering and aging heat treatment on part alloy powder to obtain an automobile part product;
the powder pretreatment is to mix the powder with high polymer plastic, wherein the plastic is any one of paraffin and polyvinyl alcohol; the addition amount of the plastic accounts for 1-5wt% of the powder.
As a preferable scheme, the preparation method of the automobile part with excellent thermal shock resistance is characterized by comprising the following steps of: the part alloy powder is prepared by one of an air atomization method, a water atomization method and a water-air combined atomization method.
As a preferable scheme, the preparation method of the automobile part with excellent thermal shock resistance is characterized by comprising the following steps of: the average particle size of the part alloy powder is 6-20 um.
As a preferable scheme, the preparation method of the automobile part with excellent thermal shock resistance is characterized by comprising the following steps of: the molding is any one of compression molding, cold isostatic pressing and injection molding; the molding pressure of the compression molding is 200-500 MPa, and the pressure maintaining time is 20-50 min; the molding pressure of the cold isostatic pressing is 200-400 MPa, and the pressure maintaining time is 20-40 min; the injection temperature of injection molding is 120-180 ℃, the injection pressure is 70-140 MPa, the injection speed is 50-110 g/s, and the mold temperature is 30-70 ℃.
As a preferable scheme, the preparation method of the automobile part with excellent thermal shock resistance is characterized by comprising the following steps of: the sintering process comprises the following steps: at vacuum degree less than or equal to 10 -2 And in a vacuum environment of Pa, heating to 1300-1400 ℃ at a heating rate of 5-10 ℃/min, preserving heat for 1-4 h, then introducing argon, rapidly cooling to 100 ℃ at 20-50 ℃/min, and discharging.
As a preferable scheme, the preparation method of the automobile part with excellent thermal shock resistance is characterized by comprising the following steps of: the aging process comprises the following steps: at vacuum degree less than or equal to 10 -2 And in a vacuum environment of Pa, heating to 400-600 ℃ at a heating rate of 5-10 ℃/min, preserving heat for 4-10 h, and then cooling to room temperature in air or quenching oil and discharging.
The invention relates to an automobile part with excellent thermal shock resistance and a preparation method thereof, which is characterized in that: the retention rate of the flexural strength of the obtained automobile part product is more than or equal to 90 percent. The method for measuring the retention rate of flexural strength is referred to the test method for thermal shock resistance of YB 4018-1991 refractory products.
Principle and advantages
The invention breaks through the preparation technology of the automobile part with excellent thermal shock resistance, and adopts the synergistic effect of the powder metallurgy and the heat treatment technology for the first time to prepare the part alloy microstructure with the ultrahigh flexural strength retention rate.
The thermal shock failure is related to the reliability of alloy materials in the service environment, and the deep research of failure criteria and failure mechanisms is necessary. Currently, thermal damage theory is the most representative thermal shock failure criterion. And (3) a process of crack initiation and propagation until failure when the material is impacted by heat, namely, when the thermal elastic strain energy stored in the material exceeds the surface energy required for forming a new surface in the process of crack initiation and propagation, the crack initiation and propagation causes damage to the material. Crack initiation and propagation are very closely related to the organization of the material. The relationship between the crystal grain size, the second phase, the impurity content and the porosity and the thermal shock resistance is analyzed one by one, and an ideal microstructure is obtained through the optimization of the preparation process.
Relationship between grain size and thermal shock resistance. The finer the grain size of the matrix, the more the grain boundaries pass through for a certain distance of crack propagation, the more the number of times of deflection of propagation paths, so that the crack propagation difficulty is increased, and the thermal shock resistance of the alloy is naturally improved. In the process of technical development, the invention performs a great deal of work on the refinement of the alloy grain size. In the aspect of component design, a proper amount of Al and Ti are added in a compounding way, so that grains can be refined, and finer-granularity powder can be synchronously selected. In the aspect of process design, the growth of crystal grains is avoided by controlling the sintering temperature and the cooling rate. Under the process parameters, an alloy microstructure with fine and uniform crystal grains (30-50 um in size) can be obtained, and the thermal shock resistance of the material is improved. The method for measuring the grain size is described in GB/T6394-2017 method for measuring average grain size of metals.
Relationship of second phase particles to thermal shock resistance. In the aging process, nano-scale second phase particles are dispersed and separated from a matrix, dislocation lines can bend around the second phase particles during plastic deformation, so that the lattice deformation energy of a dislocation influence area is increased, the resistance of dislocation line movement is increased, the slip resistance is increased, the effects of pinning dislocation and blocking dislocation migration are achieved, the strength of a material is greatly improved, the higher the inherent strength of the material is, the higher the strength of the material which is not damaged due to thermal stress is, and the thermal shock resistance is good. The inventors have unexpectedly found three precipitated phases: ni (Ni) 3 Mo、Fe 2 Mo、Ni 3 Ti and the particle size of the Ti is 50-200 nm, which is helpful for improving the strength and thermal shock resistance of the material, so that the microstructure containing the precipitated phases is obtained by applying proper aging temperature and heat preservation time, and the thermal shock resistance of the part is further improved.
Relationship between impurity content and thermal shock resistance. The alloy of parts, in particular the alloy of martensite matrix, has extremely high sensitivity to the number, performance and morphology of C, O, N, P, S, si and Mn and other harmful impurity elements and inclusions because of the hard and brittle matrix and low fracture toughness. These trace elements are likely to form a compound with elements such as Mo and Ti, and segregate at grain boundaries to cause a sharp decrease in toughness, i.e., a hot embrittlement phenomenon. The better the fracture toughness, the more stable the cyclic deformation response and the better the plastic deformation capability of the material, and the better the thermal shock resistance is shown. It was found that the raw material itself is the largest source of the introduced impurities throughout the process. Therefore, the impurity content of the powder is greatly reduced by optimizing the atomization powder making process, the content of paraffin or polyvinyl alcohol is controlled to be 1-5% in a smaller range, and the impurity elements such as C, O, S are prevented from being remained by the higher vacuum degree, the slower heating rate and the longer heat preservation time, so that the precondition for obtaining the material with high thermal shock resistance is achieved.
Relation between porosity and thermal shock resistance. Generally, the smaller the thermal expansion coefficient is, the smaller the volume change of the material caused by temperature change is, and the smaller the corresponding temperature stress is, the better the thermal shock resistance is; the thermal conductivity is large, the smaller the temperature difference inside the material is, the smaller the stress difference caused by the temperature difference is, and the better the thermal shock resistance is. The inventor surprisingly found that by adjusting a proper amount of porosity through controlling the sintering process, the surface heat transfer coefficient is improved, the convection effect is increased, but too many pores affect the strength of the matrix, so that the porosity is finally determined to be 3-7% through a large number of experiments, and not only can the enough thermal shock resistance be ensured, but also the strength of the alloy is not affected.
Compared with the prior art, the invention has the following advantages:
1) Excellent performance. The thermal shock resistance is equivalent to that of a ceramic material, and the requirements of automobile parts are well met;
2) The working procedure is simple, and the production efficiency is high;
3) The coating-free plastic processing technology has high difficulty, and is easy for mass production.
In conclusion, the microstructure with finer matrix grains, nanometer second phase, low impurity content and proper porosity is prepared by adopting the synergistic effect of the powder metallurgy and the heat treatment technology, the preparation technology of the automobile part with excellent thermal shock resistance is broken through, the thermal shock resistance of the alloy is greatly improved, the process is simple, the cost is low, the mass production is easy, and the requirements of the automobile part can be well met.
Drawings
Fig. 1 is a metallographic photograph of an aged alloy.
Fig. 2 is an SEM morphology of the aged alloy.
Fig. 3 is a TEM topography of the second phase.
Detailed Description
The process according to the invention is further described below in connection with three examples.
And preparing the alloy powder of the automobile part according to the design components, and sequentially carrying out pretreatment, forming, sintering and aging heat treatment to obtain the automobile part product.
Example 1:
an automobile part with excellent thermal shock resistance and a preparation method thereof are provided, and the process is as follows:
A. and (3) component design: co:12wt.%, ni:13wt.%, mo:6wt.% Ti:1wt.%, balance Fe, wherein the impurity content is C:0.02wt.%, O:0.01wt.%, N:0.02wt.%, P:0.02wt.%, S:0.04wt.%, si:0.09wt.% and Mn:0.05wt.%;
B. powder preparation: preparing part alloy powder by using an air atomization method, wherein the average particle size is 12um;
C. pretreatment: mixing the powder with paraffin, wherein the addition amount of the paraffin accounts for 2wt.% of the powder;
D. shaping: placing the pretreated powder into a die, performing compression molding, and maintaining the pressure for 40min by using 400MPa molding pressure to obtain a blank;
E. sintering: placing the blank into a vacuum sintering furnace, and keeping the vacuum degree less than or equal to 10 -2 Heating to 1350 ℃ at a heating rate of 5 ℃/min in a vacuum environment of Pa, preserving heat for 2 hours, then introducing argon, rapidly cooling to 100 ℃ at 30 ℃/min, and discharging;
F. aging: in the heat treatment furnace, the vacuum degree is less than or equal to 10 -2 Heating to 500 ℃ at a heating rate of 5 ℃/min under a vacuum environment of Pa, preserving heat for 4 hours, and then cooling to room temperature in air;
G. and (3) performance detection: the retention of flexural strength was 92%.
Example 2:
an automobile part with excellent thermal shock resistance and a preparation method thereof are provided, and the process is as follows:
A. and (3) component design: co:12wt.%, ni:14wt.%, mo:5wt.% Ti:0.5wt.%, al:1.2wt.% Fe, balance, wherein the impurity content is C:0.02wt.%, O:0.01wt.%, N:0.01wt.%, P:0.03wt.%, S:0.04wt.%, si:0.1wt.% and Mn:0.06wt.%;
B. powder preparation: preparing part alloy powder with an average granularity of 8um by using a water atomization method;
C. pretreatment: mixing the powder with paraffin, wherein the addition amount of the paraffin accounts for 2wt.% of the powder;
D. shaping: placing the pretreated powder into a sheath of a cold isostatic press, cold isostatic pressing, and maintaining the pressure for 30min by using a forming pressure of 300MPa to obtain blanks;
E. sintering: placing the blank into a vacuum sintering furnace, and keeping the vacuum degree less than or equal to 10 -2 Heating to 1360 ℃ at a heating rate of 5 ℃/min under a vacuum environment of Pa, preserving heat for 2 hours, then introducing argon, rapidly cooling to 100 ℃ at 35 ℃/min, and discharging;
F. aging: in the heat treatment furnace, the vacuum degree is less than or equal to 10 -2 Heating to 480 ℃ at a heating rate of 5 ℃/min under a vacuum environment of Pa, preserving heat for 6 hours, then placing the mixture in quenching oil, cooling to room temperature, and discharging;
G. and (3) performance detection: the retention of flexural strength was 94%.
Example 3:
an automobile part with excellent thermal shock resistance and a preparation method thereof are provided, and the process is as follows:
A. and (3) component design: co:10wt.%, ni:12wt.%, mo:6wt.% Al:0.5wt.% Fe, balance, wherein the impurity content is C:0.02wt.%, O:0.01wt.%, N:0.02wt.%, P:0.03wt.%, S:0.03wt.%, si:0.09wt.% and Mn:0.03wt.%;
B. powder preparation: preparing part alloy powder with an average particle size of 10um by using a water-gas combined atomization method;
C. pretreatment: mixing the powder with polyvinyl alcohol, wherein the addition amount of the polyvinyl alcohol accounts for 3wt.% of the powder;
D. shaping: injecting the pretreated powder on an injection molding machine to obtain a blank, wherein the injection temperature is 150 ℃, the injection pressure is 90MPa, the injection speed is 60g/s, and the mold temperature is 60 ℃;
E. sintering: placing the blank into a vacuum sintering furnace, and keeping the vacuum degree less than or equal to 10 -2 Heating to 1370 ℃ at a heating rate of 5 ℃/min in a vacuum environment of Pa, preserving heat for 2 hours, then introducing argon, rapidly cooling to 100 ℃ at 40 ℃/min, and discharging;
F. aging: in the heat treatment furnace, the vacuum degree is less than or equal to 10 -2 Heating to 450 ℃ at a heating rate of 5 ℃/min under a vacuum environment of Pa, preserving heat for 8 hours, and then cooling to room temperature in air;
G. and (3) performance detection: the retention of flexural strength was 91%.
Comparative examples 1-1:
the only difference from example 2 is that the alloy composition does not contain Ti and Al, and the detection performance and flexural strength retention are 75%. Probably due to the lack of Ti and Al, the crystal grains grow up, and the thermal shock resistance is affected.
Comparative examples 1-2:
the only difference from example 2 is that the alloy powder has an average particle size of 30um, a test property and a flexural strength retention of 74%. Probably because the coarse powder causes the grain growth, the thermal shock resistance is affected.
Comparative example 2-1:
the only difference from example 2 is the S content of 0.1wt.%, the test performance, flexural strength retention of 72%. Probably due to the formation of metal sulfides with excessive S content, the fracture toughness is reduced, and the thermal shock resistance is further affected.
Comparative example 2-2:
the only difference from example 2 is the C content of 0.1wt.%, the test performance, the flexural strength retention of 73%. Probably due to the formation of metal carbides with excessive C content, fracture toughness is reduced, thereby affecting thermal shock resistance.
Comparative example 3:
the above examples are merely preferred embodiments of the present invention and are not intended to limit the scope of the invention, and other equivalent changes, modifications, substitutions and combinations of parts or elements according to the principles and teachings of the invention are intended to be included within the scope of the invention.
Claims (8)
1. An automobile part with excellent thermal shock resistance is characterized by comprising the following chemical components: co: 8-15 wt.% of Ni:13 to 20wt.% of Mo:5 to 10wt.% of Al:0 to 5wt.% of Ti:0 to 5wt.% of Fe and the balance of unavoidable impurity elements, the total amount of the impurity elements being less than or equal to 0.3wt.%;
the microstructure includes a matrix and a second phase;
the matrix is any one of martensite and austenite;
the grain size of the matrix is 30-50 um;
the second phase is distributed in the matrix;
the chemical composition of the second phase is Ni 3 Mo、Fe 2 Mo、Ni 3 At least one of Ti;
the particle size of the second phase is 50-200 nm;
the relative density of the automobile part is 93% -97%.
2. An automotive part having excellent thermal shock resistance according to claim 1, wherein: the impurity element contains at least one of C, O, N, P, S, si and Mn in mass percent; wherein the content of C is less than or equal to 0.03 wt%, the content of O is less than or equal to 0.01 wt%, the content of N is less than or equal to 0.02 wt%, the content of P is less than or equal to 0.04 wt%, the content of S is less than or equal to 0.04 wt%, the content of Si is less than or equal to 0.1 wt% and the content of Mn is less than or equal to 0.05 wt%.
3. The method for producing an automobile part excellent in thermal shock resistance according to claim 1 or 2, comprising the steps of: the method comprises the steps of sequentially carrying out pretreatment, forming, sintering and aging heat treatment on part alloy powder to obtain an automobile part product;
the powder pretreatment is to mix the powder with high polymer plastic, wherein the plastic is any one of paraffin and polyvinyl alcohol; the addition amount of the plastic accounts for 1-5 wt.% of the powder;
the average granularity of the alloy powder of the part is 6-20 um;
the forming is any one of compression molding, cold isostatic pressing and injection molding; the forming pressure of the cold isostatic pressing is 200-400 MPa, and the pressure maintaining time is 20-40 min.
4. The method for manufacturing an automobile part with excellent thermal shock resistance according to claim 3, wherein: the part alloy powder is prepared by one of an air atomization method, a water atomization method and a water-air combined atomization method.
5. The method for manufacturing an automobile part with excellent thermal shock resistance according to claim 3, wherein: the molding pressure of the compression molding is 200-500 MPa, and the pressure maintaining time is 20-50 min; the injection temperature of the injection molding is 120-180 ℃, the injection pressure is 70-140 MPa, the injection speed is 50-110 g/s, and the mold temperature is 30-70 ℃.
6. The method for manufacturing an automobile part with excellent thermal shock resistance according to claim 3, wherein: the sintering process comprises the following steps: at vacuum degree less than or equal to 10 -2 Heating to 1300-1400 ℃ at a heating rate of 5-10 ℃/min under the vacuum environment of Pa, preserving heat for 1-4 h, then introducing argon, rapidly cooling to 100 ℃ at 20-50 ℃/min, and discharging.
7. The method for manufacturing an automobile part with excellent thermal shock resistance according to claim 3, wherein: the aging process comprises the following steps: at vacuum degree less than or equal to 10 -2 Heating to 400-600 ℃ at a heating rate of 5-10 ℃/min under the vacuum environment of Pa, preserving heat for 4-10 h, and then cooling to room temperature in air or quenching oil and discharging.
8. The method for producing an automobile part having excellent thermal shock resistance according to any one of claims 1 or 2 or an automobile part having excellent thermal shock resistance according to any one of claims 3 to 7, characterized in that: the retention rate of the flexural strength of the obtained automobile part product is more than or equal to 90 percent.
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| US3369892A (en) * | 1965-08-20 | 1968-02-20 | Chromalloy American Corp | Heat-treatable nickel-containing refractory carbide tool steel |
| US3522115A (en) * | 1968-08-02 | 1970-07-28 | Burgess Norton Mfg Co | Powder metallurgy method of forming an age hardenable ferrous alloy |
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