钛合金动态断裂韧性测试方法及断裂行为的研究
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摘要
本文研究了测试钛合金材料动态断裂韧性的试验方法,分别探索了适用于示波冲击法和焦散线法两种测试方法的试样形式。采用示波冲击法对TA15ELI合金、TC4合金、TB10合金的Ⅰ型载荷动态断裂韧性进行了测试,采用焦散线法对TA15ELI合金Ⅱ型载荷动态断裂韧性及平均裂纹扩展速率进行了测试,分析了落锤／摆锤加载系统下钛合金动态起裂过程和影响钛合金动态断裂性能的组织因素。
对于示波冲击法测试钛合金动态断裂韧性的研究表明：不同组织类型的钛合金有不同的缺口敏感性,因而为了简化制样工艺的U型切口试样不适用于动态断裂韧性测试。在落锤或摆锤系统示波冲击测试涉及的加载速率范围内,钛合金一般在屈服之后发生动态断裂。带有a/w=0.2左右较短预制疲劳裂纹的Charpy冲击试样能够适用于示波冲击试验测试Ⅰ型载荷动态断裂韧性Jd。
对于焦散线法测试钛合金动态断裂韧性的研究表明：在落锤系统所能达到的加载速率范围内难以测试钛合金平面应力条件Ⅰ型载荷动态断裂韧性。两端切口试样能够适用于焦散线法测试钛合金平面应力条件Ⅱ型载荷动态断裂韧性及动态裂纹扩展平均速率。焦散线法测得TA15ELI合金片层组织的试样平面应力条件Ⅱ型裂纹动态断裂韧性为279MPa-m1/2, II型裂纹的平均扩展速度为32.6m/s。
TA15ELI、TC4、TB10三种合金通过热处理可以获得的最高动态断裂韧性Jd处于近似水平,其中TA15ELI合金略高。TA15ELI、TC4合金的魏氏组织,TC4合金(a+B转)组织、a’马氏体组织以及TB10合金的(弥散a相+β基体)组织通过组织细节参数的调整可以获得较高的动态断裂韧性,Jd数值在350-400kJ/m2范围。TA15ELI合金的魏氏组织相对于片层组织有更低的缺口敏感性和更高的动态断裂韧性。TC4合金(等轴a+a’马氏体)组织以及TB10合金的(a”马氏体+β基体)组织动态断裂韧性较差。
钛合金类型及组织形态影响其动态断裂模式。片层组织的TA15ELI合金、(a+B转)组织的TC4合金、(a+a’马氏体)组织的TC4合金、(弥散a+β基体)TB10合金以混合模式发生动态断裂,但以韧性模式为主,断口由大量韧窝组成。魏氏组织的TA15ELI合金及a’马氏体组织的TC4合金、(a”马氏体+β基体)组织的TB10合金的断口呈现解理特征,但魏氏组织断口的解离面周围包含大量的细小韧窝。对于Ⅱ型动态断裂,片层组织TA15ELI合金断口由沿剪切方向拉长的韧窝以及光滑的弯曲小平面组成。在裂纹起裂过程中存在剪切集中化区域。
钛合金断口表面存在大量的显微孔洞和二次裂纹,在动态断裂过程中,显微孔洞的生成能够起到耗散冲击能量的作用。a相内部靠近相界面处为显微孔洞形核位置。起裂过程以显微孔洞聚合的方式形成断裂面。
钛合金动态断裂韧性受等轴相a含量及a相片层形貌等组织细节的交互影响。对于(a+β转)组织的TC4合金,其动态断裂韧性受等轴a相含量及次生a相片层形貌等组织细节的交互影响,等轴a相含量宜控制在47-50%范围。次生a相应控制其形貌为短棒状。
In this paper, the measurement of dynamic fracture toughness for titanium alloys was studied. The dimensions of the specimens as well as pre-nocth or pre-crack, which were suitable for either instrumented impact test or caustics method, were determined by a series of experiments. The dynamic fracture toughness under mode-I loading of TA15ELI, TC4 and TB10 alloys were evaluated by instrumented impact test, while the caustics method was adoped to test mode-Ⅱdynamic fracture toughness and averge velocity of crack propagating for TA15ELI alloy in plane-stress condition. It is also discussed that the effects of microstructure factors on dynamic fracture toughness.
The results of study on instrumented impact test are shown as following:The dynamic fracture property for titanium alloys exhibits sensitivity to the notch-tip radius. Thus, the use of U-notched specimen for simplification is inappropriate for evaluating dynamic fracture toughness. The fracture of specimens usually happens after yield for titanium alloys. The Charpy specimen with short pre-crack (a/w=0.2) shows its feasibility for evaluating mode-I dynamic fracture toughness Jd by the method of instrumented impact test.
The results of study on caustics method are shown as following:it is difficult to determine dynamic fracture toughness for titanium alloys in mode-I plane-stress condition in the loading rate extent that can be introduced by drop hammer system, while both dynamic fracture toughness and averge velocity of crack propagation in mode-Ⅱplane-stress condition can be tested by specimen with pre-notch in two sides. For TA15ELI alloy with lath-like microstructure, the dynamic fracture toughness K11d is 279MPa-m1/2, and the averge velocity of crack propagating is 32.6m/s.
The respectively highest dynamic fracture toughness Jd values of TA15ELI, TC4 and TB10 alloys are in a similar level, in which the value of TA15ELI is higher. TA15ELI and TC4 alloy with Widmanstatten microstructure, TC4 alloy with (a+BβTrans) microstructure, TC4 alloy with a'martensite microstructure, and TB10 alloy with (distributed a+βmatrix) microstructure, the specimens with above types of microstructures can develop a better dynamic fracture property by microstructure parameter controlling, which show the Jd values about 350～400kJ/m2. TA15ELI alloy with Widmanstatten microstructure has a better dynamic fracture and lower notch sensitivity than that with lath-like microstructure. TC4 alloy with (a+a'martensite) microstructure and TB10 alloy with (a" martensite+βmatrix) exhibit poor dynamic fracture toughness.
The dynamic fracture mode is influenced by alloy brand and microsturecture. TA15ELI alloy with lath-like microstructure, TC4 alloy with (a+βTans) microstructure, TC4 alloy with (a+a'martensite) microstructure, and TB10 alloy with (distributed a+βmatrix) microstructure, the specimens with above types of microstructures have a ductile and brittle mixed fracture (mainly ductile) under dynamic loading. The fracture surfaces are composed of dimples and tear ridges. TA15ELI alloy with Widmanstatten microstructure, TC4 alloy with a'martensite microstructure and TB10 alloy with (a" martensite+13 matrix) microstructure, the fracture of specimens with above microstructures shows a cleavage features, but for Widmanstatten microstructure the edges of cleavage facets are covered with very fine dimples. For mode-Ⅱfracture, The fracture behavior of TA15ELI alloy under mode-Ⅱdynamic loading in this experiment has a feature of mixed mode, mainly plastic and partly brittle. The fracture surface is composed of elongated dimple along loading direction and smoothly curved facet. Shear localization exists in the crack initiation process.
It can be found a large amount of micro-voids as well as secondary micro-cracks on the fracture sureface. These voids play a role of energy dissipation in the dynamic fracture process when the voids nucleate. Micro-voids nucleate at phase boundaries in a phase. Fracture surface initiation results from voids coalescence.
For TC4 alloy with (a+βTans) microstructure, the dynamic fracture toughness is influenced by microstructure details, such as volume of equiaxed a Phase and ratio of length/width for secondary a Phase; the value of volume of equiaxed a in 47～50% with short rod-like secondary a Phase leads to relative good dynamic fracture toughness in this experiment.
对于示波冲击法测试钛合金动态断裂韧性的研究表明：不同组织类型的钛合金有不同的缺口敏感性,因而为了简化制样工艺的U型切口试样不适用于动态断裂韧性测试。在落锤或摆锤系统示波冲击测试涉及的加载速率范围内,钛合金一般在屈服之后发生动态断裂。带有a/w=0.2左右较短预制疲劳裂纹的Charpy冲击试样能够适用于示波冲击试验测试Ⅰ型载荷动态断裂韧性Jd。
对于焦散线法测试钛合金动态断裂韧性的研究表明：在落锤系统所能达到的加载速率范围内难以测试钛合金平面应力条件Ⅰ型载荷动态断裂韧性。两端切口试样能够适用于焦散线法测试钛合金平面应力条件Ⅱ型载荷动态断裂韧性及动态裂纹扩展平均速率。焦散线法测得TA15ELI合金片层组织的试样平面应力条件Ⅱ型裂纹动态断裂韧性为279MPa-m1/2, II型裂纹的平均扩展速度为32.6m/s。
TA15ELI、TC4、TB10三种合金通过热处理可以获得的最高动态断裂韧性Jd处于近似水平,其中TA15ELI合金略高。TA15ELI、TC4合金的魏氏组织,TC4合金(a+B转)组织、a’马氏体组织以及TB10合金的(弥散a相+β基体)组织通过组织细节参数的调整可以获得较高的动态断裂韧性,Jd数值在350-400kJ/m2范围。TA15ELI合金的魏氏组织相对于片层组织有更低的缺口敏感性和更高的动态断裂韧性。TC4合金(等轴a+a’马氏体)组织以及TB10合金的(a”马氏体+β基体)组织动态断裂韧性较差。
钛合金类型及组织形态影响其动态断裂模式。片层组织的TA15ELI合金、(a+B转)组织的TC4合金、(a+a’马氏体)组织的TC4合金、(弥散a+β基体)TB10合金以混合模式发生动态断裂,但以韧性模式为主,断口由大量韧窝组成。魏氏组织的TA15ELI合金及a’马氏体组织的TC4合金、(a”马氏体+β基体)组织的TB10合金的断口呈现解理特征,但魏氏组织断口的解离面周围包含大量的细小韧窝。对于Ⅱ型动态断裂,片层组织TA15ELI合金断口由沿剪切方向拉长的韧窝以及光滑的弯曲小平面组成。在裂纹起裂过程中存在剪切集中化区域。
钛合金断口表面存在大量的显微孔洞和二次裂纹,在动态断裂过程中,显微孔洞的生成能够起到耗散冲击能量的作用。a相内部靠近相界面处为显微孔洞形核位置。起裂过程以显微孔洞聚合的方式形成断裂面。
钛合金动态断裂韧性受等轴相a含量及a相片层形貌等组织细节的交互影响。对于(a+β转)组织的TC4合金,其动态断裂韧性受等轴a相含量及次生a相片层形貌等组织细节的交互影响,等轴a相含量宜控制在47-50%范围。次生a相应控制其形貌为短棒状。
In this paper, the measurement of dynamic fracture toughness for titanium alloys was studied. The dimensions of the specimens as well as pre-nocth or pre-crack, which were suitable for either instrumented impact test or caustics method, were determined by a series of experiments. The dynamic fracture toughness under mode-I loading of TA15ELI, TC4 and TB10 alloys were evaluated by instrumented impact test, while the caustics method was adoped to test mode-Ⅱdynamic fracture toughness and averge velocity of crack propagating for TA15ELI alloy in plane-stress condition. It is also discussed that the effects of microstructure factors on dynamic fracture toughness.
The results of study on instrumented impact test are shown as following:The dynamic fracture property for titanium alloys exhibits sensitivity to the notch-tip radius. Thus, the use of U-notched specimen for simplification is inappropriate for evaluating dynamic fracture toughness. The fracture of specimens usually happens after yield for titanium alloys. The Charpy specimen with short pre-crack (a/w=0.2) shows its feasibility for evaluating mode-I dynamic fracture toughness Jd by the method of instrumented impact test.
The results of study on caustics method are shown as following:it is difficult to determine dynamic fracture toughness for titanium alloys in mode-I plane-stress condition in the loading rate extent that can be introduced by drop hammer system, while both dynamic fracture toughness and averge velocity of crack propagation in mode-Ⅱplane-stress condition can be tested by specimen with pre-notch in two sides. For TA15ELI alloy with lath-like microstructure, the dynamic fracture toughness K11d is 279MPa-m1/2, and the averge velocity of crack propagating is 32.6m/s.
The respectively highest dynamic fracture toughness Jd values of TA15ELI, TC4 and TB10 alloys are in a similar level, in which the value of TA15ELI is higher. TA15ELI and TC4 alloy with Widmanstatten microstructure, TC4 alloy with (a+BβTrans) microstructure, TC4 alloy with a'martensite microstructure, and TB10 alloy with (distributed a+βmatrix) microstructure, the specimens with above types of microstructures can develop a better dynamic fracture property by microstructure parameter controlling, which show the Jd values about 350～400kJ/m2. TA15ELI alloy with Widmanstatten microstructure has a better dynamic fracture and lower notch sensitivity than that with lath-like microstructure. TC4 alloy with (a+a'martensite) microstructure and TB10 alloy with (a" martensite+βmatrix) exhibit poor dynamic fracture toughness.
The dynamic fracture mode is influenced by alloy brand and microsturecture. TA15ELI alloy with lath-like microstructure, TC4 alloy with (a+βTans) microstructure, TC4 alloy with (a+a'martensite) microstructure, and TB10 alloy with (distributed a+βmatrix) microstructure, the specimens with above types of microstructures have a ductile and brittle mixed fracture (mainly ductile) under dynamic loading. The fracture surfaces are composed of dimples and tear ridges. TA15ELI alloy with Widmanstatten microstructure, TC4 alloy with a'martensite microstructure and TB10 alloy with (a" martensite+13 matrix) microstructure, the fracture of specimens with above microstructures shows a cleavage features, but for Widmanstatten microstructure the edges of cleavage facets are covered with very fine dimples. For mode-Ⅱfracture, The fracture behavior of TA15ELI alloy under mode-Ⅱdynamic loading in this experiment has a feature of mixed mode, mainly plastic and partly brittle. The fracture surface is composed of elongated dimple along loading direction and smoothly curved facet. Shear localization exists in the crack initiation process.
It can be found a large amount of micro-voids as well as secondary micro-cracks on the fracture sureface. These voids play a role of energy dissipation in the dynamic fracture process when the voids nucleate. Micro-voids nucleate at phase boundaries in a phase. Fracture surface initiation results from voids coalescence.
For TC4 alloy with (a+βTans) microstructure, the dynamic fracture toughness is influenced by microstructure details, such as volume of equiaxed a Phase and ratio of length/width for secondary a Phase; the value of volume of equiaxed a in 47～50% with short rod-like secondary a Phase leads to relative good dynamic fracture toughness in this experiment.
引文
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