A non-contact heating apparatus uses a series of rotating magnets to heat, levitate, and/or move metal articles therethrough. A first series of rotating magnets heats the metal article to a desired temperature. A second series of rotating magnets levitates the metal article within the heating apparatus and maintains desired tension in the metal article, including urging the metal article through the heating apparatus. The heating apparatus can extend sufficiently far to soak the metal article at the desired temperature for a desired duration. The rotating magnets can be positioned outside of an electrically non-conductive, heat resistant chamber filled with an inert or mildly reactive gas, through which the metal article passes in the heating apparatus.

The present invention provides a heat treatment jig. A metal wire as a heat treatment target is to be wound around the jig. The jig comprises a cylindrical tubular body whose outer wall surface has a helical groove formed along a circumferential direction to wind the metal wire. A depth of the groove is larger than a length at which the metal wire will isolate from the groove when the metal wire wound along the groove at room temperature is thermally expanded by being heated to a predetermined heat treatment temperature.

The present invention provides a heat treatment jig. A metal wire as a heat treatment target is to be wound around the jig. The jig comprises a cylindrical tubular body whose outer wall surface has a helical groove formed along a circumferential direction to wind the metal wire. A depth of the groove is larger than a length at which the metal wire will isolate from the groove when the metal wire wound along the groove at room temperature is thermally expanded by being heated to a predetermined heat treatment temperature.

A steam turbine rotor blade achieving both abrasion resistance and reliability, and a method for manufacturing a steam turbine rotor blade capable of obtaining such a steam turbine rotor blade are provided. A steam turbine rotor blade according to the invention is characterized by including a blade base material and an erosion shield formed on a surface of the blade base material, wherein the blade base material is composed of a titanium alloy, and the erosion shield is composed of a weld overlay layer including a parent phase composed of pure titanium in which a metal element is solid-dissolved or a titanium alloy in which a metal element is solid-dissolved, and a hard phase dispersed in the parent phase.

A method of refining a microstructure of a titanium material can include providing a solid titanium material at a temperature below about 400 C. The titanium material can be heated under a hydrogen-containing atmosphere to a hydrogen charging temperature that is above a transus temperature of the titanium material and below a melting temperature of the titanium material, and held at this temperature for a time sufficient to convert the titanium material to a substantially homogeneous phase. The titanium material can be cooled under the hydrogen-containing atmosphere to a phase transformation temperature below the transus temperature and above about 400 C., and held for a time to produce phase regions. The titanium material can also be held under a substantially hydrogen-free atmosphere or vacuum at a dehydrogenation temperature below the transus temperature and above the phase decomposition temperature to remove hydrogen from the titanium material.

A method of refining a microstructure of a titanium material can include providing a solid titanium material at a temperature below about 400 C. The titanium material can be heated under a hydrogen-containing atmosphere to a hydrogen charging temperature that is above a transus temperature of the titanium material and below a melting temperature of the titanium material, and held at this temperature for a time sufficient to convert the titanium material to a substantially homogeneous phase. The titanium material can be cooled under the hydrogen-containing atmosphere to a phase transformation temperature below the transus temperature and above about 400 C., and held for a time to produce phase regions. The titanium material can also be held under a substantially hydrogen-free atmosphere or vacuum at a dehydrogenation temperature below the transus temperature and above the phase decomposition temperature to remove hydrogen from the titanium material.

The disclosure provides a fine-grain tin-phosphor bronze alloy strip and a preparation method thereof. The fine-grain tin-phosphor bronze alloy strip comprises the following elements in percentage by mass: 4.0-10 wt % of Sn, 0.01-0.3 wt % of P and the balance of Cu and inevitable impurity elements, the average grain size of the tin-phosphor bronze alloy strip is 1-3 m, the grain size is in normal distribution, and the standard deviation of the grain size is 0.9 m or below; the proportion of the total low-CSL grain boundary in the tin-phosphor bronze alloy strip in the whole grain boundary is 66-74%, and in the total low-CSL grain boundary, the ratio range of (9+27)/3 is 0.12-0.23:1. The fine-grain tin-phosphor bronze alloy strip of this disclosure enables a finished strip can have the tensile strength and the excellent bending performance at the same time.

The disclosure provides a fine-grain tin-phosphor bronze alloy strip and a preparation method thereof. The fine-grain tin-phosphor bronze alloy strip comprises the following elements in percentage by mass: 4.0-10 wt % of Sn, 0.01-0.3 wt % of P and the balance of Cu and inevitable impurity elements, the average grain size of the tin-phosphor bronze alloy strip is 1-3 m, the grain size is in normal distribution, and the standard deviation of the grain size is 0.9 m or below; the proportion of the total low-CSL grain boundary in the tin-phosphor bronze alloy strip in the whole grain boundary is 66-74%, and in the total low-CSL grain boundary, the ratio range of (9+27)/3 is 0.12-0.23:1. The fine-grain tin-phosphor bronze alloy strip of this disclosure enables a finished strip can have the tensile strength and the excellent bending performance at the same time.

The disclosure provides a modified tin-phosphor bronze alloy and a preparation method thereof. The modified tin-phosphor bronze alloy comprises the following elements in percentage by mass: 4.0-10 wt % of Sn, 0.01-0.3 wt % of P and the balance of Cu and inevitable impurity elements, the average grain size of the modified tin-phosphor bronze alloy is 1-3 m, the grain size is in normal distribution, and the standard deviation of the grain size is below 0.8 m; the proportion of the total low-CSL grain boundary in the modified tin-phosphor bronze alloy in the whole grain boundary is 66-74%, and in the total low-CSL grain boundary, the ratio range of (9+27)/3 is (0.12-0.23):1. The modified tin-phosphor bronze alloy of this disclosure enables a finished alloy can give consideration to both tensile strength and excellent bending performance.

The disclosure provides a modified tin-phosphor bronze alloy and a preparation method thereof. The modified tin-phosphor bronze alloy comprises the following elements in percentage by mass: 4.0-10 wt % of Sn, 0.01-0.3 wt % of P and the balance of Cu and inevitable impurity elements, the average grain size of the modified tin-phosphor bronze alloy is 1-3 m, the grain size is in normal distribution, and the standard deviation of the grain size is below 0.8 m; the proportion of the total low-CSL grain boundary in the modified tin-phosphor bronze alloy in the whole grain boundary is 66-74%, and in the total low-CSL grain boundary, the ratio range of (9+27)/3 is (0.12-0.23):1. The modified tin-phosphor bronze alloy of this disclosure enables a finished alloy can give consideration to both tensile strength and excellent bending performance.