CN114921692A - Production method of high-strength wear-resistant titanium-aluminum-tin composite material capable of efficiently blocking tin exudation - Google Patents
Production method of high-strength wear-resistant titanium-aluminum-tin composite material capable of efficiently blocking tin exudation Download PDFInfo
- Publication number
- CN114921692A CN114921692A CN202210551163.3A CN202210551163A CN114921692A CN 114921692 A CN114921692 A CN 114921692A CN 202210551163 A CN202210551163 A CN 202210551163A CN 114921692 A CN114921692 A CN 114921692A
- Authority
- CN
- China
- Prior art keywords
- aluminum
- tin
- alloy
- titanium
- percent
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Granted
Links
Images
Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C21/00—Alloys based on aluminium
- C22C21/003—Alloys based on aluminium containing at least 2.6% of one or more of the elements: tin, lead, antimony, bismuth, cadmium, and titanium
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B32—LAYERED PRODUCTS
- B32B—LAYERED PRODUCTS, i.e. PRODUCTS BUILT-UP OF STRATA OF FLAT OR NON-FLAT, e.g. CELLULAR OR HONEYCOMB, FORM
- B32B15/00—Layered products comprising a layer of metal
- B32B15/01—Layered products comprising a layer of metal all layers being exclusively metallic
- B32B15/017—Layered products comprising a layer of metal all layers being exclusively metallic one layer being formed of aluminium or an aluminium alloy, another layer being formed of an alloy based on a non ferrous metal other than aluminium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C14/00—Alloys based on titanium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C21/00—Alloys based on aluminium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/02—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working in inert or controlled atmosphere or vacuum
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B32—LAYERED PRODUCTS
- B32B—LAYERED PRODUCTS, i.e. PRODUCTS BUILT-UP OF STRATA OF FLAT OR NON-FLAT, e.g. CELLULAR OR HONEYCOMB, FORM
- B32B2307/00—Properties of the layers or laminate
- B32B2307/50—Properties of the layers or laminate having particular mechanical properties
- B32B2307/554—Wear resistance
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B32—LAYERED PRODUCTS
- B32B—LAYERED PRODUCTS, i.e. PRODUCTS BUILT-UP OF STRATA OF FLAT OR NON-FLAT, e.g. CELLULAR OR HONEYCOMB, FORM
- B32B2419/00—Buildings or parts thereof
-
- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
- Y02P10/00—Technologies related to metal processing
- Y02P10/20—Recycling
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Metal Rolling (AREA)
Abstract
The invention discloses a production method of a high-strength wear-resistant titanium-aluminum-tin composite material for efficiently blocking tin exudation, which comprises the following steps: firstly, coating the composite alloy aluminum on the outer layer of the aluminum-tin alloy, then carrying out high-temperature heat treatment, then carrying out heat compounding with the titanium strip, and finally carrying out diffusion annealing treatment. The invention breaks through important bottleneck, solves the problem of tin leakage, and realizes the purpose of no loss of tin element which is difficult to realize in the process of research and development for many years.
Description
Technical Field
The invention belongs to the technical field of metal material preparation, and particularly relates to a production method of a high-strength wear-resistant titanium-aluminum-tin composite material for efficiently blocking tin exudation.
Background
The tin element is added in smelting, and the tin is used as the most important indispensable element in alloy components, so that the occlusion resistance and the abrasion resistance of the alloy material can be improved, the abrasion with other components is reduced, and the heat productivity is reduced. The melting point of tin element is low, tin is added during alloy smelting, the tin can be completely fused in a liquid state to form eutectic, the content of the eutectic is generally lower than 20%, but when the heat treatment temperature exceeds 200 ℃, the tin is easy to be separated out in an alpha phase, crystallized on the surface of the alloy, and peeled off during cooling, so that the tin element in the alloy is lost, commonly called tin leakage. The loss or tin running of tin element is easy to cause the problems of reduced wear-resisting index, unstable composite interface, low composite strength, low annealing temperature, low elongation of material and the like of the material.
The rare metal titanium is a silvery white, expensive and difficult-to-process special material, and is characterized by light density, high strength, strong corrosion resistance and wear resistance, wherein, aluminum is a main alloy element of titanium alloy, and has obvious effects on improving the normal temperature and high temperature strength of the alloy, reducing the specific gravity, increasing the elastic modulus, resisting the wear and the like.
The early production process of the aluminum-titanium alloy adopts fusion casting and die casting molding, but the components of the alloy are unstable, the cast is easy to generate holes, fracture and the like, the requirement of high component proportion is difficult to realize, and the strength is far lower than that of a layered composite material.
Aluminum tin 20 copper-titanium composite layered metal as a novel high-end wear-resistant material is gradually popularized in application under extreme environments, but no effective solution is available at present for solving the problem of tin leakage.
Disclosure of Invention
In order to solve the technical problems of separation of tin element, loss of tin component, low heat treatment temperature, poor material performance, infirm layered composite interface and the like in the heat treatment process of the aluminum-tin 20-copper composite strip in the prior art, the invention aims to provide a production method of a high-strength wear-resistant titanium-aluminum-tin composite material for efficiently blocking tin exudation.
In order to achieve the purpose and achieve the technical effect, the invention adopts the technical scheme that:
the production method of the high-strength wear-resistant titanium-aluminum-tin composite material for efficiently blocking tin exudation comprises the steps of wrapping and compounding the outer layer of an aluminum-tin alloy, then carrying out heat treatment at the heat treatment temperature higher than the heat treatment temperature (200 ℃ and below) in the conventional process, then carrying out heat compounding with a titanium belt, and finally carrying out diffusion annealing treatment to efficiently block tin loss.
The production method of the high-strength wear-resistant titanium-aluminum-tin composite material for efficiently blocking tin exudation comprises the following steps:
(1) surface deoxidation pretreatment of aluminum-tin alloy
(2) And (2) coating the aluminum-tin alloy obtained in the step (1) with a composite aluminum layer
(3) Heat treatment of
(4) And thermally compounding with the titanium strip
(5) Aluminum-titanium composite interface diffusion annealing
(6) And making a finished product.
Further, in the step (1), the aluminum-tin alloy is aluminum-tin 20 copper, and the aluminum-tin 20 copper is a hot-rolled coil, and the aluminum-tin alloy comprises the following chemical components: cu 0.7-1.3%, Sn 17.5-22.5%, Ni 0.1%, Si 0.7%, Fe 0.7%, Mn 0.7%, Ti 0.2%, other elements 0.5%, and Al in balance, and milling the surface layer and two side surfaces of the aluminum-tin 20 copper with the thickness of 0.5-1.0mm after the deoxidation pretreatment.
Further, in the step (2), alloy aluminum is mixed on the upper surface and the lower surface of the aluminum-tin alloy obtained in the step (1).
Further, the aluminum 3003 is matched on the upper surface and the lower surface of the aluminum-tin alloy obtained in the step (1), the aluminum-tin alloy and the aluminum 3003 are subjected to double-sided laminated compounding in a warm rolling preheating mode, the proportion of the aluminum-tin alloy and the aluminum 3003 wrapping the composite alloy is less than 2%, the preheating temperature of the aluminum-tin alloy is 100-180 ℃, the preheating temperature of the aluminum-tin alloy 3003 is 80-100 ℃, the composite rolling deformation rate is less than 15%, and the rolling speed is controlled to be 20-30 m/min.
Further, the alloy aluminum 3003 comprises the following chemical components: less than or equal to 0.6 percent of Si, less than or equal to 0.7 percent of Fe, 0.05-0.2 percent of Cu, 1.0-1.5 percent of Mn, less than or equal to 0.1 percent of Zn, and the balance of Al.
Further, in the step (3), a resistance wire open-hearth heating mode is adopted for heat treatment, the atmosphere in the furnace is vacuum negative pressure of-0.02 Pa, the heat treatment temperature is 450-520 ℃, the temperature is higher than that in the conventional process, the heat treatment holding time is 4-8h, the tapping temperature is lower than 60 ℃, and the tin content in the aluminum-tin alloy is detected by sampling after heat treatment.
Further, in the step (4), when the aluminum-tin alloy is thermally compounded with the titanium strip, the heating temperature of the aluminum-tin alloy is 400-450 ℃, the heating temperature of the titanium strip is 150-220 ℃, the compound rolling deformation rate is 15-28%, and the compound rolling speed is 8-15 m/min.
Further, TA1 is selected as the titanium strip, and the titanium strip mainly comprises the following chemical components: fe is less than or equal to 0.25 percent, C is less than or equal to 0.10 percent, N is less than or equal to 0.03 percent, H is less than or equal to 0.015 percent, O is less than or equal to 0.20 percent, and the balance is Ti.
Further, in the step (5), a hood-type annealing furnace is adopted for interface diffusion annealing, the annealing temperature is 480-520 ℃, the heat preservation time is 8-12h, and the atmosphere in the furnace is more than or equal to 99.99% of argon.
Compared with the prior art, the invention has the following beneficial effects:
according to the invention, firstly, the surface of an aluminum-tin alloy (aluminum-tin 20 copper and the like) is coated with alloy aluminum, then, the aluminum-tin alloy is subjected to heat treatment, and then, functional rare metals such as titanium and the like are compounded, so that the effects of keeping the required alloy components and material properties and improving the compound strength are achieved, and thus, an alloy layer finished product with higher tin, high wear resistance, high strength, good plasticity and high compound interface strength is obtained, high economic benefits are achieved, and the product requirements of high-end markets and severe environments are met.
The invention breaks through important bottleneck, solves the problem of tin leakage, and realizes the purpose of no loss of tin element which is difficult to realize in the process of research and development for many years.
The invention effectively solves the problem that the aluminum tin 20 copper is annealed and tin runs, namely tin crystals seep out to reduce the wear resistance of the alloy material, solves the problem that the composite strength of a layered interface after the aluminum tin 20 copper is compounded with a titanium strip is low, provides a more superior alloy material for the fields of wear resistance and high strength, can be widely applied to the fields of engineering, mining metallurgy, construction and the like with particularly severe working conditions, high material strength requirements and good wear resistance, and can be used for preparing mechanical products such as bearings, bearing bushes, brake pads, mining machinery, conveying bent structures and the like.
Drawings
FIG. 1 is a process flow diagram of the present invention;
FIG. 2 is a graph showing the result of the bleeding of tin element during the heat treatment in different temperature zones according to the present invention
FIG. 3 is a graph showing tin deposition on the surface of Al-Sn 20Cu during the heat treatment of the wrapped composite Al layer at an annealing temperature of 490 ℃ in example 3 of the present invention;
FIG. 4 is a graph showing tin deposition on the surface of aluminum tin 20 copper during heat treatment of an unwrapped composite aluminum layer in comparative example 2 at an annealing temperature of 320 ℃.
Detailed Description
The present invention is described in detail below so that the advantages and features of the present invention can be more easily understood by those skilled in the art, and thus the scope of the present invention can be clearly and clearly defined.
The following presents a simplified summary of one or more aspects in order to provide a basic understanding of such aspects. This summary is not an extensive overview of all contemplated aspects, and is intended to neither identify key or critical elements of all aspects nor delineate the scope of any or all aspects. Its sole purpose is to present some concepts of one or more aspects in a simplified form as a prelude to the more detailed description that is presented later.
The production method of the high-strength wear-resistant titanium-aluminum-tin composite material capable of efficiently blocking tin seepage can prevent tin crystals in the titanium-aluminum-tin nonzero copper composite material from seeping, the method firstly wraps and compounds the outer layer of the aluminum-tin alloy, namely, aluminum (including 3XXX series and the like) in a micro proportion is utilized to wrap and compound aluminum-tin nonzero copper (AlSn20Cu) firstly, so that tin elements are blocked from being separated out during annealing, the heat treatment temperature can be increased by nearly 300 ℃ compared with the heat treatment temperature in the prior art, the composite interface strength is enhanced, the seepage proportion of the tin crystals is obviously reduced, and the wear resistance of the aluminum-tin alloy is improved; and compounding the aluminum-tin-di-zero copper compounded with the aluminum or the aluminum alloy with the titanium strip by heating and vacuum.
As shown in fig. 1-4, the production method of the high-strength wear-resistant titanium-aluminum-tin composite material for efficiently blocking tin exudation specifically comprises the following steps:
(1) and performing surface deoxidation pretreatment on the aluminum-tin alloy:
the aluminum-tin alloy is preferably aluminum-tin-20 copper, and the aluminum-tin-20 copper is selected from a hot-rolled coil, and comprises the following chemical components: 0.7-1.3% of Cu, 17.5-22.5% of Sn, 0.1% of Ni, 0.7% of Si, 0.7% of Fe, 0.7% of Mn, 0.2% of Ti, 0.5% of other elements and the balance of Al, wherein the specification is 15-20.0 x 300-800mm, the surface oil stain layer is cleaned and dried, impurities such as surface oxides and the like are processed by adopting a process blank to mill the surface, and the thickness of the surface and two side surfaces is milled to be 0.5-1.0 mm;
(2) and a wrapping type composite aluminum layer:
the specification of the aluminum tin 20 copper subjected to the surface treatment in the step (1) is 14.5-19.5 x 300-: si is less than or equal to 0.6 percent, Fe is less than or equal to 0.7 percent, Cu is 0.05-0.2 percent, Mn is 1.0-1.5 percent, Zn is less than or equal to 0.1 percent, and the balance of Al is 0.15-0.2 x 300-800 mm; the proportion of the wrapped composite single-layer alloy aluminum is less than 2 percent; the double-sided laminated compounding is carried out by adopting a warm rolling preheating mode, the preheating temperature of aluminum tin 20 copper is 100-180 ℃, the preheating temperature of alloy aluminum 3003 is 80-100 ℃, and the compound rolling deformation rate is less than 15%; the rolling speed is controlled to be 20m/min-30 m/min;
(3) and (3) heat treatment:
performing heat treatment after the coating and compounding in the step (2), wherein the heat treatment adopts a resistance wire open-hearth heating mode, the atmosphere in the furnace is vacuum negative pressure of-0.02 Pa, the heat treatment temperature is 450-520 ℃, the heat treatment temperature is obviously higher than that in the conventional process, the heat treatment heat preservation time is 4-8h, and the tapping temperature is lower than 60 ℃; after heat treatment, sampling and detecting the content of tin element in the aluminum tin 20 copper, wherein the precipitation ratio of tin element is shown in figure 2 in the heat treatment process at different temperatures, as can be seen from figure 2, the ratio of the aluminum tin 20 copper surface layer coated with the composite alloy aluminum monolayer is below 2%, when the heat treatment temperature is increased to about 300 ℃ to 520 ℃, the precipitation ratio of tin element is only about 1.7%, and is reduced by about 22.8% compared with the tin precipitation of the uncoated composite aluminum layer at the same temperature, the leaching depth of tin element is 0.05-0.08mm, the thickness of surface aluminum is 0.10-0.15mm, and the tin leakage phenomenon is effectively prevented;
(4) and thermally compounding with the titanium strip:
(41) after the annealing treatment in the step (3), a polishing disc is distributed on the surface of the Al-AlSn20Cu-Al, an oxide layer on the surface of the aluminum is treated, and the depth of the polished surface is less than 5 mu m; the titanium strip is preferably TA1, and the chemical composition of the titanium strip is mainly as follows: fe is less than or equal to 0.25 percent, C is less than or equal to 0.10 percent, N is less than or equal to 0.03 percent, H is less than or equal to 0.015 percent, O is less than or equal to 0.20 percent, the balance is Ti, the specification of the strip is 0.3-1.0 mm/300-800 mm, and the surface is subjected to acid pickling treatment on oxide;
(42) and Al-AlSn20Cu-Al + TA1, wherein the heating temperature of the aluminum-tin alloy is 400-450 ℃, the heating temperature of the titanium strip is 150-220 ℃, and the phenomena of high-temperature oxidation, nitridation and hydrogen absorption of titanium are avoided. Single-layer or double-layer titanium strip materials can be adopted for compounding, the compound rolling deformation rate is 15-28%, and the compound rolling speed is 8-15 m/min;
(5) and aluminum-titanium composite interface diffusion annealing:
after the steps are combined, the layered metal coiled strip is subjected to alloy layer interface diffusion by adopting a hood-type annealing furnace; the annealing temperature is 480-520 ℃, the heat preservation time is 8-12h, and the atmosphere in the furnace is more than or equal to 99.99 percent of argon;
(6) and the finished product can be finely rolled to 0.2-3.0mm according to the requirement, and the thickness is different.
Example 1
The production method of the high-strength wear-resistant titanium-aluminum-tin composite material for efficiently blocking tin exudation comprises the following steps:
(1) and (3) carrying out surface deoxidation pretreatment on the aluminum tin 20 copper:
the aluminum tin 20 copper is selected from a hot rolling billet coil, and the chemical components of the hot rolling billet coil are as follows: 0.7% of Cu, 20.7% of Sn, 0.1% of Ni, 0.7% of Si, 0.7% of Fe, 0.7% of Mn, 0.2% of Ti, 0.5% of other elements, and the balance of Al: the specification is 20.0 × 500mm, the surface oil stain layer is cleaned on the surface and then dried, impurities such as surface oxides and the like are processed by a process blank milling machine, the thickness of the surface layer and two side surfaces is milled to be 0.5 × 499.5mm, and the specification of a finished product is changed into 19.5 × 499.5 mm;
(2) and a wrapped composite aluminum layer:
on a multi-metal layered composite rolling mill (800mm) unit, the upper and lower surfaces of the aluminum-tin 20 copper subjected to surface treatment in the step (1) are respectively matched with alloy aluminum 300, and the chemical component proportion is as follows: 0.6% of Si, 0.7% of Fe, 0.05% of Cu, 1.0% of Mn, 0.1% of Zn and the balance of Al, wherein the specification is 0.15 x 520 mm; the proportion of the wrapping composite single-layer aluminum layer is 0.76%; performing double-sided laminated compounding by adopting a warm rolling preheating mode, wherein the preheating temperature of aluminum tin 20 copper is 130 ℃, the preheating temperature of alloy aluminum 3003 series is 100 ℃, the thickness of the coated and compounded aluminum tin copper is 18.0mm, and the compound rolling deformation rate is 8.4%; the rolling speed is controlled at 25 m/min;
(3) and (3) heat treatment:
performing heat treatment after wrapping and compounding, wherein the heat treatment adopts a resistance wire open hearth heating mode, the atmosphere in the furnace is vacuum negative pressure of-0.02 Pa, the heat treatment temperature is 470 ℃, the heat treatment heat preservation time is 6h, and the tapping temperature is lower than 55 ℃; after heat treatment, sampling and detecting that the content of tin element in the aluminum tin 20 copper is about 20.5 percent;
(4) and thermally compounding with the titanium strip:
(41) the Al-AlSn20Cu-Al surface after heat treatment and annealing is coated with a polishing disk to treat an oxide layer on the surface of the aluminum, and the depth of a polished surface is 2 mu m; selecting TA1 as a titanium strip, selecting 0.5mm x 500mm as the specification of the strip, and carrying out acid cleaning treatment on the surface of the strip to obtain an oxide; the titanium strip material adopts TA1, and the chemical components of the titanium strip material are as follows: 0.25% of Fe, 0.10% of C, 0.03% of N, 0.015% of H, 0.20% of O and the balance of Ti;
(42) and Al-AlSn20Cu-Al + TA1, wherein the heating temperature of the aluminum-tin alloy is 400 ℃, the heating temperature of the titanium strip is 180 ℃, the composite heating titanium layer is protected by high-purity argon, and the air flow is 60 cubic/hour. The single-layer strips are compounded, the thickness of a compounded finished product is 15.0mm, the compound rolling deformation rate is 18.9 percent, and the compound rolling speed is 10 m/min;
(5) and (3) aluminum-titanium diffusion annealing:
carrying out alloy layer interface diffusion on the laminated metal coiled strip by adopting a hood-type annealing furnace after the compounding; the annealing temperature is 500 ℃, the heat preservation time is 10 hours, and the atmosphere in the furnace is more than or equal to 99.99 percent of argon;
(6) finished product finish rolling and trimming specification of 0.8 x 450mm, weight of single coil of strip is less than 3 tons, surface wear resistance of finished product material is NM520, and peel strength is 32N/mm 2 The elongation was 31.5%.
Example 2
The production method of the high-strength wear-resistant titanium-aluminum-tin composite material for efficiently blocking tin exudation comprises the following steps:
(1) and (3) carrying out deoxidation pretreatment on the surface of the aluminum tin 20 copper:
the aluminum tin 20 copper is selected from a hot rolling billet coil, and the chemical components of the hot rolling billet coil are as follows: 21.3% of Sn, 0.1% of Cu 1.0% of Ni, 0.7% of Si, 0.7% of Fe, 0.7% of Mn, 0.2% of Ti, 0.5% of other elements and the balance of Al, wherein the specification is 18.0 x 650mm, the surface oil stain layer is cleaned and dried, the impurity layer such as surface oxide is processed by a process blank milling machine, the thickness of the surface layer and two side surfaces is milled to be 0.8mm, and the specification of a finished product is 17.2 x 649.2 mm.
(2) And a wrapping type composite aluminum layer:
on a multi-metal laminated composite rolling mill (800mm) unit, the upper surface and the lower surface of the aluminum-tin 20 copper after surface treatment are respectively matched with alloy aluminum 3003 with the specification of 0.2 x 655 mm; the proportion of the wrapped composite single-layer aluminum layer is 1.16 percent; performing double-sided laminated compounding by adopting a warm rolling preheating mode, wherein the preheating temperature of aluminum tin 20 copper is 150 ℃, the preheating temperature of alloy aluminum 3003 series is 120 ℃, the thickness of the coated and compounded aluminum tin is 15.5mm, and the compound rolling deformation rate is 10.9%; the rolling speed is controlled at 20 m/min;
(3) and (3) heat treatment:
performing heat treatment after wrapping and compounding, wherein the heat treatment adopts a resistance wire open hearth heating mode, the atmosphere in the furnace is vacuum negative pressure of-0.02 Pa, the heat treatment temperature is 520 ℃, the heat treatment heat preservation time is 5h, and the tapping temperature is lower than 55 ℃; after heat treatment, sampling and detecting that the content of tin element in the aluminum tin 20 copper is about 21.0 percent;
(4) and compounding the aluminum-tin-20-copper composite coil with the titanium coiled tape:
(41) the Al-AlSn20Cu-Al surface after heat treatment and annealing is coated with a polishing disc to treat an oxide layer on the surface of the aluminum, and the depth of the polished surface is less than 5 mu m; selecting TA1 as a titanium strip, selecting 1.0mm 650mm as the specification of the strip, and carrying out acid cleaning treatment on the surface of the strip to obtain an oxide;
(42) Al-AlSn20Cu-Al + TA1, wherein the heating temperature of the aluminum-tin alloy is 430 ℃, the heating temperature of the titanium strip is 160 ℃, the composite heating titanium layer is protected by high-purity argon, and the gas flow is 70 cubic/hour. The single-layer strips are adopted for compounding, the thickness of a compounded finished product is 13.0mm, the compound rolling deformation rate is 21.2%, and the compound rolling speed is 15 m/min;
(5) and aluminum-titanium diffusion annealing:
the laminated metal coiled strip after the compounding is subjected to alloy layer interface diffusion by adopting a hood-type annealing furnace; the annealing temperature is 480 ℃, the heat preservation time is 12 hours, and the atmosphere in the furnace is more than or equal to 99.99 percent of argon;
(6) finished product finish rolling, the cut edge specification is 1.2 x 620mm, the weight of a single coil of strip is less than 5 tons, the surface wear resistance of the finished product material is NM530, and the peel strength is 36.5N/mm 2 And the elongation is 29.5%.
The same as in example 1.
Example 3
The difference between this example and example 2 is that the annealing temperature in the aluminum-titanium diffusion annealing of this example is 490 ℃, and the tin deposition on the aluminum tin 20 copper surface is shown in fig. 3.
Comparative example 1
The comparative example is different from the example 2 in that the step (2) is not carried out, the heat treatment is directly carried out after the aluminum tin 20 copper surface deoxidation pretreatment of the complete step (1), the aluminum tin 20 copper composite roll and the titanium coiled tape are compounded, and the aluminum-titanium diffusion annealing is carried out.
Comparative example 2
The comparative example is different from the example 2 in that the comparative example does not carry out the step (2), the heat treatment is directly carried out after the aluminum tin 20 copper surface deoxidation pretreatment of the complete step (1), the aluminum tin 20 copper composite roll and the titanium coiled tape are compounded, the aluminum-titanium diffusion annealing is carried out, the annealing temperature in the aluminum-titanium diffusion annealing is 320 ℃, and the tin precipitation on the aluminum tin 20 copper surface is shown in figure 4. As can be seen from fig. 3-4, the tin deposition on the surface of the aluminum-tin 20 copper of the non-wrapped composite aluminum layer is more serious than that of the aluminum-tin 20 copper of the wrapped composite aluminum layer, i.e., the tin leakage of the aluminum-tin 20 copper is effectively blocked by the wrapped composite aluminum alloy at an increased heat treatment temperature.
The wear resistance and interfacial composite strength of the products of example 2 and comparative example 2 were tested and the results are shown in table 1:
TABLE 1
From the above, after the aluminum-tin 20 copper surface layer is wrapped by the composite alloy aluminum layer, the tin element precipitation phenomenon is inhibited, the tin leakage problem is solved, and the wear-resisting level, the composite interface strength, the elongation and the like are obviously improved.
The parts or structures of the invention which are not described in detail can be the same as those in the prior art or the existing products, and are not described in detail herein.
The above description is only an embodiment of the present invention, and not intended to limit the scope of the present invention, and all modifications of equivalent structures and equivalent processes, which are made by the present specification, or directly or indirectly applied to other related technical fields, are included in the scope of the present invention.
Claims (10)
1. The production method of the high-strength wear-resistant titanium-aluminum-tin composite material for efficiently blocking tin exudation is characterized in that the outer layer of aluminum-tin alloy is wrapped and compounded, then heat treatment is carried out, and then the aluminum-tin alloy is thermally compounded with a titanium strip, and finally diffusion annealing treatment is carried out.
2. The production method of the high-strength wear-resistant titanium-aluminum-tin composite material for efficiently blocking tin exudation according to claim 1, comprising the following steps:
(1) surface deoxidation pretreatment of aluminum-tin alloy
(2) Wrapping the aluminum-tin alloy obtained in the step (1) to form a composite aluminum layer
(3) Heat treatment of
(4) And thermally compounding with the titanium strip
(5) Aluminum-titanium composite interface diffusion annealing
(6) And making a finished product.
3. The production method of the high-strength wear-resistant titanium-aluminum-tin composite material for efficiently blocking tin exudation, according to claim 1, wherein in the step (1), the aluminum-tin alloy is aluminum-tin 20 copper, and the aluminum-tin 20 copper is a hot-rolled coil, and comprises the following chemical components: cu 0.7-1.3%, Sn 17.5-22.5%, Ni 0.1%, Si 0.7%, Fe 0.7%, Mn 0.7%, Ti 0.2%, other elements 0.5%, and Al in balance, and milling the surface layer and two side surfaces of the aluminum-tin 20 copper with the thickness of 0.5-1.0mm after the deoxidation pretreatment.
4. The production method of the high-strength wear-resistant titanium-aluminum-tin composite material for efficiently blocking tin exudation, according to claim 1, wherein in the step (2), alloy aluminum is mixed on the upper surface and the lower surface of the aluminum-tin alloy obtained in the step (1).
5. The production method of the high-strength wear-resistant titanium-aluminum-tin composite material for efficiently blocking tin exudation, according to claim 4, is characterized in that alloy aluminum 3003 is proportioned on the upper and lower surfaces of the aluminum-tin alloy obtained in the step (1), the aluminum-tin alloy and the alloy aluminum 3003 are subjected to double-sided layered compounding by adopting a warm rolling preheating mode, the proportion of the coated composite alloy aluminum 3003 is less than 2%, the preheating temperature of the aluminum-tin alloy is 100-180 ℃, the preheating temperature of the alloy aluminum 3003 is 80-100 ℃, the composite rolling deformation rate is less than 15%, and the rolling speed is controlled within 20-30 m/min.
6. The production method of the high-strength wear-resistant titanium-aluminum-tin composite material for efficiently blocking tin exudation according to claim 5, wherein the alloy aluminum 3003 comprises the following chemical components: less than or equal to 0.6 percent of Si, less than or equal to 0.7 percent of Fe, 0.05-0.2 percent of Cu, 1.0-1.5 percent of Mn, less than or equal to 0.1 percent of Zn, and the balance of Al.
7. The production method of the high-strength wear-resistant titanium-aluminum-tin composite material for efficiently blocking tin exudation, according to claim 2, is characterized in that in the step (3), a resistance wire open hearth heating mode is adopted for heat treatment, the furnace atmosphere is vacuum negative pressure of-0.02 Pa, the heat treatment temperature is 450 ℃ -520 ℃, the heat treatment holding time is 4-8h, the tapping temperature is lower than 60 ℃, and the tin element content in the aluminum-tin alloy is detected by sampling after heat treatment.
8. The method for producing the high-strength wear-resistant titanium-aluminum-tin composite material capable of effectively blocking tin exudation according to claim 2, wherein in the step (4), when the titanium strip is thermally compounded, the heating temperature of the aluminum-tin alloy is 400-450 ℃, the heating temperature of the titanium strip is 150-220 ℃, the compound rolling deformation rate is 15-28%, and the compound rolling speed is 8-15 m/min.
9. The production method of the high-strength wear-resistant titanium-aluminum-tin composite material capable of effectively blocking tin exudation according to claim 8, wherein TA1 is selected from the titanium strip, and the chemical components of the TA1 are mainly as follows: fe is less than or equal to 0.25 percent, C is less than or equal to 0.10 percent, N is less than or equal to 0.03 percent, H is less than or equal to 0.015 percent, O is less than or equal to 0.20 percent, and the balance is Ti.
10. The production method of the high-strength wear-resistant titanium-aluminum-tin composite material for efficiently blocking tin exudation according to claim 2, wherein in the step (5), a hood-type annealing furnace is adopted for interface diffusion annealing, the annealing temperature is 480-520 ℃, the heat preservation time is 8-12h, and the atmosphere in the furnace is more than or equal to 99.99% of argon.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202210551163.3A CN114921692B (en) | 2022-05-20 | 2022-05-20 | Production method of high-strength wear-resistant titanium-aluminum-tin composite material capable of efficiently blocking tin exudation |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202210551163.3A CN114921692B (en) | 2022-05-20 | 2022-05-20 | Production method of high-strength wear-resistant titanium-aluminum-tin composite material capable of efficiently blocking tin exudation |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN114921692A true CN114921692A (en) | 2022-08-19 |
| CN114921692B CN114921692B (en) | 2023-03-10 |
Family
ID=82809470
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN202210551163.3A Active CN114921692B (en) | 2022-05-20 | 2022-05-20 | Production method of high-strength wear-resistant titanium-aluminum-tin composite material capable of efficiently blocking tin exudation |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN114921692B (en) |
Citations (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2001153141A (en) * | 1999-11-29 | 2001-06-08 | Ndc Co Ltd | Al-Sn BASE BEARING MATERIAL |
| JP2006346730A (en) * | 2005-06-20 | 2006-12-28 | Furukawa Sky Kk | Method for producing composite sheet with aluminum alloy-titanium groove |
| CN101450542A (en) * | 2007-11-28 | 2009-06-10 | 北京有色金属研究总院 | Laminar titanium aluminum composite plate and preparation method thereof |
| CN102744408A (en) * | 2012-07-25 | 2012-10-24 | 哈尔滨工业大学 | Preparation method of titanium aluminum-based laminated composite material plate |
| CN102935447A (en) * | 2011-08-15 | 2013-02-20 | 上海核威实业有限公司 | Aluminum tin 40 copper-steel metal bearing material and production method thereof |
| CN105316532A (en) * | 2014-08-04 | 2016-02-10 | 上海核威实业有限公司 | Manufacturing method for aluminum alloy-steel double metal material used for sliding bearing of multilayer structure |
| CN107377617A (en) * | 2017-06-14 | 2017-11-24 | 中南大学 | A kind of method for preparing multicomponent composite strip |
| CN110340173A (en) * | 2019-07-01 | 2019-10-18 | 东北轻合金有限责任公司 | A kind of preparation method of 6061 aluminium alloy and the laminated composite plate of T2 copper |
-
2022
- 2022-05-20 CN CN202210551163.3A patent/CN114921692B/en active Active
Patent Citations (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2001153141A (en) * | 1999-11-29 | 2001-06-08 | Ndc Co Ltd | Al-Sn BASE BEARING MATERIAL |
| JP2006346730A (en) * | 2005-06-20 | 2006-12-28 | Furukawa Sky Kk | Method for producing composite sheet with aluminum alloy-titanium groove |
| CN101450542A (en) * | 2007-11-28 | 2009-06-10 | 北京有色金属研究总院 | Laminar titanium aluminum composite plate and preparation method thereof |
| CN102935447A (en) * | 2011-08-15 | 2013-02-20 | 上海核威实业有限公司 | Aluminum tin 40 copper-steel metal bearing material and production method thereof |
| CN102744408A (en) * | 2012-07-25 | 2012-10-24 | 哈尔滨工业大学 | Preparation method of titanium aluminum-based laminated composite material plate |
| CN105316532A (en) * | 2014-08-04 | 2016-02-10 | 上海核威实业有限公司 | Manufacturing method for aluminum alloy-steel double metal material used for sliding bearing of multilayer structure |
| CN107377617A (en) * | 2017-06-14 | 2017-11-24 | 中南大学 | A kind of method for preparing multicomponent composite strip |
| CN110340173A (en) * | 2019-07-01 | 2019-10-18 | 东北轻合金有限责任公司 | A kind of preparation method of 6061 aluminium alloy and the laminated composite plate of T2 copper |
Non-Patent Citations (2)
| Title |
|---|
| 姜剑国等: "高性能轴瓦材料―铝锡20铜-钢双金属卷带的研制", 《内燃机配件》 * |
| 王强等: "铝合金复合材料关键技术指标与生产工艺概述", 《黑龙江冶金》 * |
Also Published As
| Publication number | Publication date |
|---|---|
| CN114921692B (en) | 2023-03-10 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN112122382B (en) | Preparation process method of wide and ultrathin cold-rolled titanium strip coil for rolling compounding | |
| CN100425717C (en) | Copper alloy for lead-wire frame and its production | |
| JPS5924179B2 (en) | Cold rolled ductile, high strength steel strip and its manufacturing method | |
| CN111270109B (en) | Method for producing 8021 aluminum alloy soft packaging foil for lithium battery by cast rolling method | |
| CN1932056A (en) | High temperature copper alloy for lead frame and its making process | |
| CN112030032B (en) | Cu-Cr-Ti-Zr alloy and copper strip preparation method | |
| WO2021046927A1 (en) | Nickel-rhenium alloy rotary tubular target material containing trace rare earth elements and preparation method therefor | |
| CN104831115A (en) | Manganese-containing brass alloy and preparation method thereof | |
| CN110983081B (en) | Method for preparing ultra-low oxygen cupronickel by adopting vacuum melting equipment | |
| CN113195777B (en) | Galvanized steel sheet excellent in plating adhesion and corrosion resistance, and method for producing same | |
| CN101654749A (en) | Easily-cutting brass and processing method of strips thereof | |
| US2768915A (en) | Ferritic alloys and methods of making and fabricating same | |
| WO2021128434A1 (en) | Easy-to-cut zinc-copper-nickel alloy, preparation method therefor and use thereof | |
| CN114921692B (en) | Production method of high-strength wear-resistant titanium-aluminum-tin composite material capable of efficiently blocking tin exudation | |
| CN1690236A (en) | Nickel silver band for piezoelectric crystal oscillator housing and method for producing same | |
| JPS62182239A (en) | Cu alloy for continuous casting mold | |
| KR101188065B1 (en) | Galvanized steel sheet having excellent coating adhesion and spot weldability and method for manufacturing the same | |
| CN116043067B (en) | High-temperature alloy material and forming method thereof | |
| JPS62182238A (en) | Cu alloy for continuous casting mold | |
| JPS6254183B2 (en) | ||
| CN115747561B (en) | Wear-resistant corrosion-resistant jewelry brass alloy and preparation method thereof | |
| CN115110326B (en) | Ti-Mo-Zr titanium alloy rope for crane and efficient preparation method thereof | |
| CN114148046B (en) | Aluminum alloy composite material and preparation method and application thereof | |
| CN110205515B (en) | Preparation method of corrosion-resistant Cu-Ni alloy | |
| CN114345935B (en) | High-speed steel rolling method |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| PB01 | Publication | ||
| PB01 | Publication | ||
| SE01 | Entry into force of request for substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| GR01 | Patent grant | ||
| GR01 | Patent grant |