CN115070021B - Method for preparing tin-lead bronze/stainless steel bimetal through directional solidification - Google Patents
Method for preparing tin-lead bronze/stainless steel bimetal through directional solidification Download PDFInfo
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Abstract
The invention discloses a method for preparing tin-lead bronze/stainless steel bimetal by directional solidification, which comprises the following steps: step 1: cutting 25Cr2MoV steel and CuSn10Pb1 alloy to remove oxide skin, and cleaning and drying with gasoline; step 2: placing the alloy treated in the step 1 into a corundum crucible and a magnesia crucible respectively, and fixing a honeycomb duct and the magnesia crucible to form a straight line; heating the corundum crucible to a certain temperature in the heat preservation area, and starting an induction power supply to smelt CuSn10Pb1; step 4: pouring molten metal into a corundum crucible, preserving heat for a certain time, and then directionally solidifying to obtain the CuSn10Pb1/25Cr2MoV steel bimetallic material after drawing.
Description
Technical Field
The invention belongs to the technical field of bimetal preparation, and relates to a method for preparing tin-lead bronze/stainless steel bimetal by directional solidification.
Background
CuSn10Pb1 alloy has excellent wear resistance and abrasion resistance, and thus is widely used as an abrasion resistant material in heavy machinery abrasion resistant parts. The 25Cr2MoV steel has good intergranular corrosion resistance and excellent impact resistance, and is widely applied to the fields of heavy machinery, pressure vessels and the like. Tin-lead bronze/steel bimetallic materials are widely used in the field of hydraulic equipment because of their excellent properties of wear resistance and high strength.
The existing method for preparing the copper/steel bimetal mainly comprises a hot-pressing diffusion connection method and a casting method, the interface strength of the copper/steel bimetal material prepared by the hot-pressing diffusion connection method is limited, and the interface is easy to crack when the copper/steel bimetal material is in service in a high-pressure environment, so that accidents such as oil leakage and the like are caused. The copper/steel bimetallic material prepared by the traditional casting method has smaller volume fraction of alpha-Cu phase at the tin-lead bronze side, disordered alpha-Cu dendrite array and inconsistent grain orientation, and a large number of hard, brittle and tin-rich phases exist among dendrites, so that the toughness of the tin-lead bronze is reduced, the friction and abrasion resistance is poor, and the service life of the bimetallic material is further influenced. As a key structural member in a hydraulic device, the copper/steel bimetallic material not only has higher interface bonding strength, but also has higher requirements on the friction and abrasion resistance of the tin-lead bronze side.
Disclosure of Invention
The invention aims to provide a method for preparing tin-lead bronze/stainless steel bimetal through directional solidification, which realizes the liquid-solid connection of CuSn10Pb1/25Cr2MoV steel bimetal and solves the problems of low bonding strength, more tin-rich phases on the tin-lead bronze side, inconsistent grain orientation, poor plasticity and poor friction and wear resistance of the copper/steel bimetal interface prepared by a hot-press diffusion connection method and a casting method in multiple aspects.
The technical scheme adopted by the invention is that the method for preparing tin-lead bronze/stainless steel bimetal by directional solidification specifically comprises the following steps:
step 1, respectively cutting 25Cr2MoV steel and CuSn10Pb1 alloy to remove surface oxide skin, processing the surfaces of the steel and the CuSn10Pb1 alloy into cylindrical bars, then respectively cleaning the 25Cr2MoV steel and the CuSn10Pb1 alloy by gasoline, and drying to obtain pretreated CuSn10Pb1 alloy and 25Cr2MoV steel;
step 2, placing the pretreated cylindrical 25Cr2MoV steel obtained in the step 1 into a cylindrical corundum crucible, placing the corundum crucible on a pull rod of a directional solidification furnace, placing the pretreated CuSn10Pb1 alloy into a magnesia crucible of an induction coil of the directional solidification furnace, and fixing a guide pipe to form a straight line with the magnesia crucible and the corundum crucible to ensure that molten metal can be poured into the corundum crucible from the magnesia crucible;
step 3, sequentially starting a mechanical pump, a Roots pump and a diffusion pump to pump vacuum in the furnace to a specified range, starting a heating power supply, heating the corundum crucible to a certain temperature in a heat preservation area, and starting an induction power supply until CuSn10Pb1 in the magnesia crucible is completely melted;
and 4, pouring molten metal into a corundum crucible to fully contact with the 25Cr2MoV steel in a turnover casting mode, starting a drawing rod according to a preset drawing rate after heat preservation is performed for a certain time, and obtaining the CuSn10Pb1/25Cr2MoV steel bimetallic material after drawing is finished.
The invention is also characterized in that:
in step 1, the gasoline cleaning specifically comprises: soaking 25Cr2MoV steel and CuSn10Pb1 alloy in a beaker filled with pure gasoline, placing the beaker in an ultrasonic cleaning instrument for ultrasonic cleaning for 10-40 min, and drying after cleaning.
In step 3, the mechanical pump, the Roots pump and the diffusion pump are sequentially started to vacuumize the furnace to 5 multiplied by 10 -3 And (3) starting a heating power supply below Pa, heating the corundum crucible in the heat preservation area to 800-1100 ℃, and starting an induction power supply to start smelting.
In the step 3, when the CuSn10Pb1 alloy is smelted, the power of the power supply is increased by 1-4 KW every 10-40 min.
In the step 4, pouring molten metal into a honeycomb duct below by adopting a turnover casting method, enabling the molten metal to flow into a corundum crucible along the honeycomb duct, and then preserving heat for 10-40 min; setting the drawing speed of the drawing rod to be 50-200 mu m/s, starting the drawing device, and obtaining the CuSn10Pb1/25Cr2MoV steel bimetallic material after the drawing is finished.
The method has the advantages that the liquid CuSn10Pb1 alloy is cast on the surface of the 25Cr2MoV steel preheated to a certain temperature, gas inclusion in molten metal is removed in the casting process, the liquid-solid connection method also promotes the CuSn10Pb1 alloy and the 25Cr2MoV steel to carry out full solute exchange to form a wider atomic diffusion layer, and the method of directional solidification is adopted to eliminate microscopic defects at the interface along with the directional migration of a solid-liquid interface, so that the CuSn10Pb1 alloy with directionally grown grains is obtained, the dual-metal liquid-solid connection of the CuSn10Pb1/25Cr2MoV steel is realized, and the problems of low bonding strength, more tin-rich phases at the side of tin-lead bronze, inconsistent grain orientation, poor plasticity and poor friction and abrasion resistance of the copper/steel dual-metal interface prepared by a hot-press diffusion connection method and a fusion casting method are solved in various aspects.
Drawings
FIG. 1 is a schematic diagram of a directional solidification system employed in a method for preparing tin-lead bronze/stainless steel bi-metal by directional solidification according to the present invention;
FIG. 2 is a diagram showing the morphology of a CuSn10Pb1/25Cr2MoV steel bimetal interface in a method for preparing tin-lead bronze/stainless steel bimetal by directional solidification according to the invention;
FIG. 3 is a diagram showing the morphology of CuSn10Pb1 side structure in a method for preparing tin-lead bronze/stainless steel bimetal by directional solidification according to the invention;
FIG. 4 is a plot of interfacial shear strength for CuSn10Pb1/25Cr2MoV steel bimetal in example 2 of a method of preparing tin-lead bronze/stainless steel bimetal by directional solidification in accordance with the present invention.
FIG. 5 is a graph of the coefficient of friction for friction and wear experiments of CuSn10Pb1 alloy and a common CuSn10Pb1 alloy in example 2 of a method for preparing tin-lead bronze/stainless steel bi-metal by directional solidification according to the present invention.
In the figure, an induction coil, a honeycomb duct, a directional solidification furnace chamber, a corundum crucible and a drawing pull rod are respectively arranged at the bottom of the furnace body, wherein the drawing is provided with the induction coil, the honeycomb duct, the directional solidification furnace chamber, the corundum crucible and the drawing pull rod.
Detailed Description
The invention will be described in detail below with reference to the drawings and the detailed description.
The invention discloses a method for preparing tin-lead bronze/stainless steel bimetal by directional solidification, which comprises the following steps:
step 1, cutting 25Cr2MoV steel to remove surface oxide skin, and processing into
The method comprises the steps of (1) cutting and removing oxide skin on the surface of CuSn10Pb1 alloy, wherein the alloy mass is 300-600 g, then soaking 25Cr2MoV steel and CuSn10Pb1 alloy in a beaker filled with pure gasoline, placing the beaker in an ultrasonic cleaning instrument, carrying out ultrasonic cleaning for 10-40 min, cleaning, drying, and obtaining pretreated CuSn10 after dryingPb1 alloy and 25Cr2MoV steel;
step 2, as shown in fig. 1, placing the pretreated cylindrical 25Cr2MoV steel obtained in the step 1 in a cylindrical corundum crucible 4, placing the corundum crucible 4 on a pull rod 5 of a directional solidification furnace chamber 3, placing the pretreated CuSn10Pb1 alloy in a magnesia crucible of an induction coil 1 in the directional solidification furnace chamber 3, and fixing a guide pipe 2 to form a straight line with the magnesia crucible and the corundum crucible to ensure that molten metal can be poured into the corundum crucible from the magnesia crucible;
the reason for using the corundum crucible in the step 2 is that the 25Cr2MoV steel contains Fe element and is easy to react with the crucible made of graphite and the like. The fixed guide pipe is in a straight line with the magnesia crucible and the corundum crucible, so that molten metal can be poured into the corundum crucible from the magnesia crucible, and finally the furnace door is closed.
Step 3, starting a mechanical pump, a Roots pump and a diffusion pump in turn to vacuumize the furnace to 5 multiplied by 10 -3 Starting a heating power supply below Pa, heating the corundum crucible in the heat preservation area to 800-1100 ℃, starting an induction power supply, starting smelting of CuSn10Pb1 alloy, increasing the power of the induction power supply by 1-4 KW every 10-40 min, increasing the power by 1-4 KW when molten metal vortex occurs in the magnesia crucible, and preserving heat for 10-40 min; the occurrence of vortex flow indicates that the fluidity of the alloy is improved, which indicates that the metal is completely melted, and the aim of continuously increasing the power is to ensure that the metal liquid obtains a certain degree of superheat, and the overheated metal liquid can improve the diffusion migration rate of solute atoms, thereby refining the alloy liquid and being beneficial to solute exchange at a copper/steel interface after casting.
The purpose of heating the corundum crucible before smelting in the step 3 is to enable Cr2MoV steel to obtain a temperature field close to the temperature of molten metal in advance, create a bottom-up temperature gradient for later directional solidification, facilitate the growth of directional solidification grains, and play a role in regulating and controlling the bimetal interface and the morphology of CuSn10Pb1 alloy.
And 4, pouring molten metal into a lower flow guide pipe by adopting a turnover casting method, enabling the molten metal to flow into a corundum crucible along the flow guide pipe, then preserving heat for 10-40 min, setting the drawing speed of a drawing rod to be 50-200 mu m/s, starting a drawing device, and obtaining the CuSn10Pb1/25Cr2MoV steel bimetallic material after drawing is finished.
The purpose of the incubation in step 4 is to make the atomic diffusion behaviour at the copper/steel interface more fully progressive. The drawing speed of the drawing rod is set to be 50-200 mu m/s, and the drawing device is started, so that the solid-liquid interface migration speed of the CuSn10Pb1 alloy can be controlled by adjusting the drawing speed, the morphology of the alloy dendrites is regulated and controlled, the grain orientation is improved to be consistent, and the CuSn10Pb1/25Cr2MoV steel bimetallic material is obtained after the drawing is finished.
As shown in FIG. 2, the visible steel side at the bimetal interface formed by the method has a slight alloying phenomenon, which indicates that the atomic migration rate is faster and the migration distance is longer in the process of compounding the CuSn10Pb1 alloy and the 25Cr2MoV steel, and the formed diffusion layer is wider.
Example 1
Step 1, cutting 25Cr2MoV steel to remove surface oxide skin, and processing into
The method comprises the steps of (1) cutting and removing oxide skin on the surface of a CuSn10Pb1 alloy, wherein the alloy mass is 300g, then soaking 25Cr2MoV steel and the CuSn10Pb1 alloy in a beaker filled with pure gasoline, placing the beaker in an ultrasonic cleaning instrument, carrying out ultrasonic cleaning for 10min, and drying after cleaning and blow-drying to obtain pretreated CuSn10Pb1 alloy and 25Cr2MoV steel;
step 2, as shown in fig. 1, placing the pretreated cylindrical 25Cr2MoV steel obtained in the step 1 in a cylindrical corundum crucible 4, placing the corundum crucible 4 on a pull rod 5 of a directional solidification furnace chamber 3, placing the pretreated CuSn10Pb1 alloy in a magnesia crucible of an induction coil 1 in the directional solidification furnace chamber 3, and fixing a guide pipe 2 to form a straight line with the magnesia crucible and the corundum crucible to ensure that molten metal can be poured into the corundum crucible from the magnesia crucible;
step 3, starting a mechanical pump, a Roots pump and a diffusion pump in turn to vacuumize the furnace to 5 multiplied by 10 -3 Starting a heating power supply below Pa, starting an induction power supply after the corundum crucible is heated to 800 ℃ in a heat preservation area, starting to smelt CuSn10Pb1 alloy, increasing the power of the induction power supply by 1KW every 10min, increasing the power by 1KW when molten metal vortex occurs in the magnesia crucible, and preserving heat10min；
And 4, pouring molten metal into a lower guide pipe by adopting a turnover casting method, enabling the molten metal to flow into a corundum crucible along the guide pipe, then preserving heat for 10min, setting the drawing speed of a drawing rod to be 50 mu m/s, starting a drawing device, and obtaining the CuSn10Pb1/25Cr2MoV steel bimetallic material after drawing. The mechanical properties of the bimetal interface are tested, and the shearing test result shows that the shearing strength of the CuSn10Pb1/25Cr2MoV steel bimetal material is 175MPa, and meanwhile, the friction and wear resistance of the CuSn10Pb1 alloy is improved, and the friction coefficient of the alloy is 0.20.
Example 2
Step 1, cutting 25Cr2MoV steel to remove surface oxide skin, and processing into
The method comprises the steps of (1) cutting and removing oxide skin on the surface of a CuSn10Pb1 alloy, wherein the alloy mass is 400g, then soaking 25Cr2MoV steel and the CuSn10Pb1 alloy in a beaker filled with pure gasoline, placing the beaker in an ultrasonic cleaning instrument, carrying out ultrasonic cleaning for 20min, and drying after cleaning and blow-drying to obtain pretreated CuSn10Pb1 alloy and 25Cr2MoV steel;
step 2, as shown in fig. 1, placing the pretreated cylindrical 25Cr2MoV steel obtained in the step 1 in a cylindrical corundum crucible 4, placing the corundum crucible 4 on a pull rod 5 of a directional solidification furnace chamber 3, placing the pretreated CuSn10Pb1 alloy in a magnesia crucible of an induction coil 1 in the directional solidification furnace chamber 3, and fixing a guide pipe 2 to form a straight line with the magnesia crucible and the corundum crucible to ensure that molten metal can be poured into the corundum crucible from the magnesia crucible;
step 3, starting a mechanical pump, a Roots pump and a diffusion pump in turn to vacuumize the furnace to 5 multiplied by 10 -3 Starting a heating power supply below Pa, starting an induction power supply after the corundum crucible is heated to 900 ℃ in a heat preservation area, starting smelting of CuSn10Pb1 alloy, increasing the power of the induction power supply by 2KW every 20min, increasing the power by 2KW when molten metal vortex occurs in the magnesia crucible, and preserving heat for 20min;
and 4, pouring molten metal into a lower guide pipe by adopting a turnover casting method, enabling the molten metal to flow into a corundum crucible along the guide pipe, then preserving heat for 20min, setting the drawing speed of a drawing rod to be 100 mu m/s, starting a drawing device, and obtaining the CuSn10Pb1/25Cr2MoV steel bimetallic material after drawing. The mechanical properties of the bimetal interface are tested, and the shearing test result shows that the shearing strength of the CuSn10Pb1/25Cr2MoV steel bimetal material is 172MPa, and meanwhile, the friction and wear resistance of the CuSn10Pb1 alloy is improved, and the friction coefficient of the alloy is 0.25.
As shown in FIG. 3, the tin-rich phase on the side of the bimetallic CuSn10Pb1 obtained after directional solidification in the embodiment 2 of the invention is obviously reduced, and the tissues are uniformly distributed in dendrites with the same orientation. The solidification interface front of the directional solidification alloy has higher temperature gradient, is favorable for generating directional crystals, obtains CuSn10Pb1 alloy with consistent grain orientation, eliminates transverse grain boundaries, solves the problems of serious solute segregation, poor plasticity, poor stamping performance and poor friction and wear resistance of the bimetallic copper alloy prepared by the traditional method, and has higher interface strength besides the excellent properties of CuSn10Pb1 alloy and 25Cr2MoV steel, the interface shearing strength can reach 170MPa, meanwhile, the friction and wear resistance of the CuSn10Pb1 alloy is improved, and the friction coefficient of the alloy is 0.25.
FIG. 4 is a plot of interfacial shear strength for CuSn10Pb1/25Cr2MoV steel bimetal in example 2 of a method of preparing tin-lead bronze/stainless steel bimetal by directional solidification in accordance with the present invention.
FIG. 5 is a graph of the coefficient of friction for friction and wear experiments of CuSn10Pb1 alloy and a common CuSn10Pb1 alloy in example 2 of a method for preparing tin-lead bronze/stainless steel bi-metal by directional solidification according to the present invention.
Example 3
Step 1, cutting 25Cr2MoV steel to remove surface oxide skin, and processing into
Cutting and removing oxide skin on the surface of CuSn10Pb1 alloy, wherein the alloy mass is 500g, then soaking 25Cr2MoV steel and CuSn10Pb1 alloy in a beaker filled with pure gasoline, placing the beaker in an ultrasonic cleaning instrument, ultrasonically cleaning for 30min, and drying after cleaning and blow-drying to obtain the copper alloyTo pretreated CuSn10Pb1 alloy and 25Cr2MoV steel;
step 2, as shown in fig. 1, placing the pretreated cylindrical 25Cr2MoV steel obtained in the step 1 in a cylindrical corundum crucible 4, placing the corundum crucible 4 on a pull rod 5 of a directional solidification furnace chamber 3, placing the pretreated CuSn10Pb1 alloy in a magnesia crucible of an induction coil 1 in the directional solidification furnace chamber 3, and fixing a guide pipe 2 to form a straight line with the magnesia crucible and the corundum crucible to ensure that molten metal can be poured into the corundum crucible from the magnesia crucible;
step 3, starting a mechanical pump, a Roots pump and a diffusion pump in turn to vacuumize the furnace to 5 multiplied by 10 -3 Starting a heating power supply below Pa, starting an induction power supply after the corundum crucible is heated to 1000 ℃ in a heat preservation area, starting to smelt CuSn10Pb1 alloy, increasing the power of the induction power supply by 3KW every 30min, increasing the power by 3KW when molten metal vortex occurs in the magnesia crucible, and preserving heat for 30min;
and 4, pouring molten metal into a lower flow guide pipe by adopting a turnover casting method, enabling the molten metal to flow into a corundum crucible along the flow guide pipe, then preserving heat for 30min, setting the drawing speed of a drawing rod to be 150 mu m/s, starting a drawing device, and obtaining the CuSn10Pb1/25Cr2MoV steel bimetallic material after drawing. The mechanical property of the bimetal interface is tested, and the shearing test result shows that the shearing strength of the CuSn10Pb1/25Cr2MoV steel bimetal material is 169MPa, and meanwhile, the friction and wear resistance of the CuSn10Pb1 alloy is improved, and the friction coefficient of the alloy is 0.23.
Example 4
Step 1, cutting 25Cr2MoV steel to remove surface oxide skin, and processing into
Cutting and removing oxide skin on the surface of CuSn10Pb1 alloy, wherein the alloy mass is 600g, then soaking 25Cr2MoV steel and CuSn10Pb1 alloy in a beaker filled with pure gasoline, placing the beaker in an ultrasonic cleaning instrument, carrying out ultrasonic cleaning for 40min, and drying after cleaning and blow-drying to obtain pretreated CuSn10Pb1 alloy and 25Cr2MoV steel;
step 2, as shown in fig. 1, placing the pretreated cylindrical 25Cr2MoV steel obtained in the step 1 in a cylindrical corundum crucible 4, placing the corundum crucible 4 on a pull rod 5 of a directional solidification furnace chamber 3, placing the pretreated CuSn10Pb1 alloy in a magnesia crucible of an induction coil 1 in the directional solidification furnace chamber 3, and fixing a guide pipe 2 to form a straight line with the magnesia crucible and the corundum crucible to ensure that molten metal can be poured into the corundum crucible from the magnesia crucible;
step 3, starting a mechanical pump, a Roots pump and a diffusion pump in turn to vacuumize the furnace to 5 multiplied by 10 -3 Starting a heating power supply below Pa, heating the corundum crucible in the heat preservation area to 800-1100 ℃, starting an induction power supply, starting smelting of CuSn10Pb1 alloy, increasing the power of the induction power supply by 4KW every 40min, increasing the power by 4KW when molten metal vortex occurs in the magnesia crucible, and preserving heat for 40min;
and 4, pouring molten metal into a lower guide pipe by adopting a turnover casting method, enabling the molten metal to flow into a corundum crucible along the guide pipe, then preserving heat for 40min, setting the drawing speed of a drawing rod to be 200 mu m/s, starting a drawing device, and obtaining the CuSn10Pb1/25Cr2MoV steel bimetallic material after drawing. The mechanical properties of the bimetal interface are tested, and the shearing test result shows that the shearing strength of the CuSn10Pb1/25Cr2MoV steel bimetal material is 170MPa, and meanwhile, the friction and wear resistance of the CuSn10Pb1 alloy is improved, and the friction coefficient of the alloy is 0.21.
The invention relates to a method for preparing tin-lead bronze/stainless steel bimetal by directional solidification, which comprises the steps of smelting CuSn10Pb1 alloy to be molten by utilizing an induction smelting method, casting molten metal on the surface of 25Cr2MoV steel, and overturning casting to effectively remove gas inclusions in the molten metal, so that the liquid CuSn10Pb1 alloy is fully contacted with the 25Cr2MoV steel, and the overheated alloy liquid and the steel are subjected to solute exchange continuously in the long-term heat preservation process, and the process is more severe due to higher superheat degree.
Claims (5)
1. A method for preparing tin-lead bronze/stainless steel bimetal by directional solidification is characterized by comprising the following steps: the method specifically comprises the following steps:
step 1, respectively cutting 25Cr2MoV steel and CuSn10Pb1 alloy to remove surface oxide skin, processing the surfaces of the steel and the CuSn10Pb1 alloy into cylindrical bars, then respectively cleaning the 25Cr2MoV steel and the CuSn10Pb1 alloy by gasoline, and drying to obtain pretreated CuSn10Pb1 alloy and 25Cr2MoV steel;
step 2, placing the pretreated cylindrical 25Cr2MoV steel obtained in the step 1 into a cylindrical corundum crucible, placing the corundum crucible on a pull rod of a directional solidification furnace, placing the pretreated CuSn10Pb1 alloy into a magnesia crucible of an induction coil of the directional solidification furnace, and fixing a guide pipe to form a straight line with the magnesia crucible and the corundum crucible to ensure that molten metal can be poured into the corundum crucible from the magnesia crucible;
step 3, sequentially starting a mechanical pump, a Roots pump and a diffusion pump to pump vacuum in the furnace to a specified range, starting a heating power supply, heating the corundum crucible to a certain temperature in a heat preservation area, and starting an induction power supply until CuSn10Pb1 in the magnesia crucible is completely melted;
and 4, pouring molten metal into a corundum crucible to fully contact with the 25Cr2MoV steel in a turnover casting mode, starting a drawing rod according to a preset drawing rate after heat preservation is performed for a certain time, and obtaining the CuSn10Pb1/25Cr2MoV steel bimetallic material after drawing is finished.
2. The method for preparing tin-lead bronze/stainless steel bimetal by directional solidification according to claim 1, wherein in the step 1, the gasoline cleaning is specifically: soaking 25Cr2MoV steel and CuSn10Pb1 alloy in a beaker filled with pure gasoline, placing the beaker in an ultrasonic cleaning instrument for ultrasonic cleaning for 10-40 min, and drying after cleaning.
3. The method for preparing tin-lead bronze/stainless steel bimetal by directional solidification according to claim 1, wherein in the step 3, a mechanical pump, a Roots pump and a diffusion pump are sequentially started to vacuum the furnace to 5×10 -3 And (3) starting a heating power supply below Pa, heating the corundum crucible in the heat preservation area to 800-1100 ℃, and starting an induction power supply to start smelting.
4. The method for preparing tin-lead bronze/stainless steel bimetal by directional solidification according to claim 1, wherein in the step 3, when the CuSn10Pb1 alloy is smelted, the power of the power supply is increased by 1-4 KW every 10-40 min.
5. The method for preparing tin-lead bronze/stainless steel bimetal by directional solidification according to claim 1, wherein in the step 4, molten metal is poured into a lower flow guide pipe by adopting a turnover casting method, flows into a corundum crucible along the flow guide pipe, and then is kept for 10-40 min; setting the drawing speed of the drawing rod to be 50-200 mu m/s, starting the drawing device, and obtaining the CuSn10Pb1/25Cr2MoV steel bimetallic material after the drawing is finished.
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Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| NL6617892A (en) * | 1965-12-21 | 1967-06-22 | ||
| CN114393197A (en) * | 2021-12-21 | 2022-04-26 | 西安理工大学 | Directional solidification preparation method of high-tin-content high-plasticity copper-tin alloy |
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Patent Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| NL6617892A (en) * | 1965-12-21 | 1967-06-22 | ||
| CN114393197A (en) * | 2021-12-21 | 2022-04-26 | 西安理工大学 | Directional solidification preparation method of high-tin-content high-plasticity copper-tin alloy |
Non-Patent Citations (1)
| Title |
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| TiAl基合金冷坩埚定向凝固研究现状与发展趋势;丁宏升;郭景杰;陈瑞润;傅恒志;;中国材料进展(第02期);20-29 * |
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