Patent Application
20250129453
The present invention relates to the technical field of titanium alloy materials, in particular to an α-type titanium alloy and its preparation method.
Titanium is an important structural metal developed in the 1950s. Titanium alloys have high strength, good corrosion resistance, and high heat resistance. Both of them have a high specific strength, good plasticity and toughness, corrosion resistance, and weldability. As aerospace materials, titanium alloys have outstanding weight loss effects, such as high-temperature titanium alloys for aero-engines and structural titanium alloys for airframes. Wherein, the room temperature strength of α-type titanium alloy is generally lower than that of β-type and α+β-type titanium alloys (but higher than that of industrial pure titanium), while the strength and transmutation at high temperature (500° C., 600° C.) are the highest among the three types of titanium alloys, with stable structure, good oxidation resistance and welding performance, corrosion resistance, and machinability, but low plasticity (thermoplasticity is still good) and poor room temperature stamping performance. With the development of aerospace technology, there are higher requirements for new and higher-performance titanium alloy materials, the α-type titanium alloy with better high-temperature tensile properties, fracture toughness, and thermal creep resistance is of great research significance.
The objective of the present invention is to provide an α-type titanium alloy and its preparation method. The α-type titanium alloy provided by the invention has excellent high-temperature tensile properties, fracture toughness, and thermal creep resistance.
In order to achieve the above objective, the present invention provides the following technical schemes:
Preferably, the α-type titanium alloy is composed of the following components in mass percentage: Al 7%˜10.6%, Zr 1.5%˜1.7%, Sn 1.8%˜2.5%, Cr 2.8%˜4.1%, Si 0.24%˜0.28%, C 0.035%˜0.048%, and the remainder is Ti and unavoidable impurity elements.
Preferably, the impurity elements are N and H, and the mass percentage of impurity elements in the α-type titanium alloy is: N≤0.05%, H≤0.01%.
The present invention also provides a preparation method for α-type titanium alloy according to the above technique, comprising the steps of:
Preferably, the melting method in step (1) is vacuum consumable arc melting.
Preferably, the temperature for blooming and forging in the step (2) is independently 950° C.˜1050° C.
Preferably, the temperature of the hot rolling in the step (3) is 890° C.˜960° C.
Preferably, the temperature of the vacuum annealing in the step (3) is 800° C.˜950° C., and the time of the vacuum annealing is 1 h˜4 h.
The present invention provides an α-type titanium alloy, the α-type titanium alloy is composed of the following components in mass percentage: Al 6.5%˜11.0%, Zr 1.3%˜1.8%, Sn 1.5%˜2.8%, Cr 2.2%˜4.5%, Si 0.2%˜0.3%, C 0.03%˜0.05%, and the remainder is Ti and inevitable impurity elements. The fracture toughness and thermal creep resistance of the prepared α-type titanium alloy are improved by controlling the content of Al, Zr, and Sn. The room temperature strength is improved by adding a certain amount of Si, and the thermal creep resistance is further improved. The addition of a certain amount of C and Cr improves the high-temperature tensile properties of the prepared α-type titanium alloy. The method provided by the invention has a simple process and low cost and can achieve good matching of low cost, high performance, and less processing capacity. The results of the examples show that the prepared α-type titanium alloy in example 1˜4 of the invention has an elastic modulus of 124˜132 GPa, a tensile strength of 867˜881 MPa, a yield strength of 743˜762 MPa, an elongation of 22%˜24.0%, and a section shrinkage of 47%˜51% at 600° C., the high-temperature tensile properties, fracture toughness and thermal creep resistance are excellent.
The present invention provides an α-type titanium alloy, the α-type titanium alloy is composed of the following components in mass percentage: Al 6.5%˜11.0%, Zr 1.3%˜1.8%, Sn 1.5%˜2.8%, Cr 2.2%˜4.5%, Si 0.2%˜0.3%, C 0.03%˜0.05%, and the remainder is Ti and inevitable impurity elements.
In the present invention, if there is no special description, the raw materials used are conventional commercially available products in the art.
In the present invention, the α-type titanium alloy is composed of the following components in mass percentage: Al 7%˜10.6%, Zr 1.5%˜1.7%, Sn 1.8%˜2.5%, Cr 2.8%˜4.1%, Si 0.24%˜0.28%, C 0.035%˜0.048%, and the remainder is Ti and unavoidable impurity elements. The fracture toughness and thermal creep resistance of the prepared α-type titanium alloy are improved by controlling the content of Al, Zr, and Sn. The room temperature strength is improved by adding a certain amount of Si, and the thermal creep resistance is further improved. The addition of a certain amount of C and Cr improves the high-temperature tensile properties of the prepared α-type titanium alloy.
In the present invention, the impurity elements are N and H, and the mass percentage of impurity elements in the α-type titanium alloy is preferably: N≤0.05%, H≤0.01%. The present invention controls the mass content of impurity elements in the above range to avoid reducing the comprehensive performance of α-type titanium alloy.
The present invention also provides a preparation method for α-type titanium alloy according to the above technique, comprising the steps of:
The present invention is based on the chemical composition of the α-type titanium alloy to be batched to obtain a titanium alloy raw material.
In the present invention, the α-type titanium alloy is composed of the following components in mass percentage: Al 6.5%˜11.0%, Zr 1.3%˜1.8%, Sn 1.5%˜2.8%, Cr 2.2%˜4.5%, Si 0.2%˜0.3%, C 0.03%˜0.05%, and the remainder is Ti and inevitable impurity elements, preferably composed of the following components: Al 7%˜10.6%, Zr 1.5%˜1.7%, Sn 1.8%˜2.5%, Cr 2.8%˜4.1%. Si 0.24%˜0.28%, C 0.035%˜0.048%, the remainder is Ti and inevitable impurity elements.
After obtaining the titanium alloy raw material, the titanium alloy raw material is successively smelted and cast to obtain an alloy ingot.
In the present invention, the melting method is vacuum consumable arc melting. The present invention has no special limitation on the melting temperature and time and can realize the full melting and mixing of each component. The present invention has no special limitation on the ingot casting method, and can adopt the technical scheme commonly used in the art.
After obtaining the alloy ingot, the alloy ingot is successively bloomed and first forged to obtain a slab.
In the present invention, the temperature for blooming and forging is preferably 950° C.˜1050° C. independently, and more preferably 960° C.˜1040° C. The present invention controls the temperature of blooming and forging to improve the high-temperature performance of the prepared α-type titanium alloy.
After obtaining the slab, the slab is subjected to successively peel and grind, hot roll, and vacuum anneal to obtain an α-type titanium alloy.
The present invention has no special limitation on the method of peeling and grinding and can adopt the technical scheme commonly used in the art.
In the present invention, the temperature of the hot rolling is preferably 890° C.˜960° C., and more preferably 900° C.˜940° C. The present invention controls the temperature of hot rolling in the above range to improve the high-temperature tensile properties and thermal creep resistance of the prepared α-type titanium alloy.
In the present invention, the vacuum annealing temperature is preferably 800° C.˜950° C., and more preferably 850° C.˜930° C. In the present invention, the vacuum annealing time is preferably 1 h˜4 h, and more preferably 2 h˜3 h. The present invention controls the temperature of vacuum annealing in the above range to improve the fracture toughness and thermal creep resistance of the prepared α-type titanium alloy.
The preparation method for α-type titanium alloy provided by the invention is simple in operation and suitable for large-scale production.
The following will describe the technical scheme in the present invention clearly and completely in combination with the examples in the invention. Obviously, the described examples are only part of the examples of the invention, not all of the examples. Based on the examples in the invention, all other examples obtained by ordinary technicians in the art without making creative labor belong to the scope of protection of the invention.
the α-type titanium alloy is composed of the following components in mass percentage: Al 7%, Zr 1.7%, Sn 2.0%, Cr 2.8%, Si 0.24%, C 0.048%, and the remainder is Ti and inevitable impurity elements.
The preparation method for α-type titanium alloy, comprises the steps of:
the α-type titanium alloy is prepared according to the method of example 1, which is different from example 1 in mass percentage, the α-type titanium alloy is composed of the following components: Al 8%, Zr 1.7%, Sn 2.5%, Cr 3.0%, Si 0.28%, C 0.048%, the remainder is Ti and inevitable impurity elements.
the α-type titanium alloy is prepared according to the method of example 1, which is different from example 1 in mass percentage, the α-type titanium alloy is composed of the following components: Al 9%, Zr 1.7%, Sn 1.8%, Cr 3.0%, Si 0.28%, C 0.048%, the remainder is Ti and inevitable impurity elements.
the α-type titanium alloy is prepared according to the method of example 1, which is different from example 1 in mass percentage, the α-type titanium alloy is composed of the following components: Al 10%, Zr 1.8%, Sn 2.5%, Cr 3.0%, Si 0.28%, C 0.048%, the remainder is Ti and inevitable impurity elements.
According to the national standard GB/T228.1˜2010, the tensile specimens are made, and the comprehensive mechanical properties at room temperature and high temperature are tested, the results are shown in Table 1.
In summary, the α-type titanium alloy prepared by examples 1˜4 of the invention have an elastic modulus of 124˜132 GPa, a tensile strength of 867˜881 MPa, a yield strength of 743˜762 MPa, an elongation of 22%˜24.0%, and a section shrinkage of 47%˜51% at 600° C., the high-temperature tensile properties, fracture toughness, and thermal creep resistance are excellent.
The above is only the preferred example of the present invention, it should be noted that for ordinary technicians in this technical field, a number of improvements and embellishments can be made without deviating from the principle of the present invention. These improvements and embellishments should also be regarded as the scope of protection of the present invention
| Number | Date | Country | Kind |
|---|---|---|---|
| 2023113663134 | Oct 2023 | CN | national |
