Sumitomo Electric Industries, Limited

Honda Giken Kogyo Kabushiki Kaisha

Honda Motor Co., Ltd.

Bosch Automotive Systems Corporation

Alps Electric Co., Ltd.

Kenji Okamoto

Hiroyuki Horimura

Masahiko Minemi

Yoshinobu Takeda

Yoshishige Takano

Toshihiko Kaji

Yoshikazu Nishiwaki

Shunji Matsuoka

Noriaki Matsumoto

Takeshi Kato

Kenichi Nonaka

Akira Kunishima

Shigeru Furuki

Masao Ichikawa

Yozo Nishiura

Kensuke Honma

Satoru Sunada

Shin-ichi Matsuzaki

Yoshimitsu Saito

Yoshihiko Higashidani

Yasushi Kida

Kenji Oogushi

Shinichi Matsuzaki

Hiroyuki Nakayama

A position detection apparatus includes a position detection target member, a magnet that moves in accordance with movement of the position detection target member, and a plurality of magnetic detectors provided on a surface opposite a movement plane of the magnet. A flat yoke is provided on the reverse face of the magnet. The magnetic polarity of a peripheral side part of the magnet is opposite to the magnetic polarity of a center part thereof. The peripheral side part is formed at a regional range that can be defined on the basis of a predetermined distance(s) measured from a side edge of the yoke.

Position detection magnet and position detection apparatus

Provided is a method of joining members having different thermal expansion coefficients, capable of joining them at a temperature lower than the melting point of Ag to obtain a joining layer having excellent durability to a thermal cycle. First Ag particleshaving an average particle diameter of 50 nm or less and an Ag foilor metal foilhaving a smaller modulus of longitudinal elasticity than that of Ag are placed between two types of membersandat least one of which has a lower thermal expansion coefficient than that of Ag, heated to join the membersand. A wax material, which is a powder mixture containing first Ag particles having an average particle diameter of 50 nm or less and second Ag particles or particles of a metal (having a modulus of longitudinal elasticity than that of Ag) having an average particle diameter of 20 &#x3bc;m or more and being contained in a volume fraction of 10 to 40% relative to a total volume of the powder mixture, is placed between the two types of membersand, heated to join the membersand. The metal foiland the particles of a metal have an Ag coating layer on a surface thereof. The first memberis formed of one type of material selected from the group consisting of Si, SiC, AlO, AlN and SiNand the second member is formed of Al or Cu.

Method of joining members having different thermal expansion coefficients

A power semiconductor module having an integral circuit board with a metal substrate electrode, an insulation substrate and a heat sink joined is disclosed. A SiC semiconductor power device is joined to a top of the metal substrate electrode of the circuit board. A difference in average coefficients of thermal expansion between constituent materials of the circuit board in a temperature range from room to joining time temperatures is 2.0 ppm/&#xb0; C. or less, and a difference in expansion, produced by a difference between a lowest operating temperature and a joining temperature, of the circuit-board constituent materials is 2,000 ppm or less.

Power semiconductor module

In a state in which a high-pressure control solenoid valve is driven to control the pressure in a common rail (refer to Step S), when the pressure in the common rail exceeds a predetermined value (refer to Step S), a driving current determined by a prescribed value map that defines the correlation between the pressure in the common rail and the driving current of the high-pressure control solenoid valve is corrected based on an actual pressure in the common rail and the driving current of the high-pressure control solenoid valve at the actual pressure (refer to Steps S, S), and the corrected driving current is passed to the high-pressure control solenoid valve, thereby ensuring appropriate and stable injection control even when there exists a variation in operational characteristics among pressure control valves.

Fuel injection device

In a state in which a high-pressure control solenoid valve is driven to control the pressure in a common rail (refer to Step S), when the pressure in the common rail exceeds a predetermined value (refer to Step S), a driving current determined by a prescribed value map that defines the correlation between the pressure in the common rail and the driving current of the high-pressure control solenoid valve is corrected based on an actual pressure in the common rail and the driving current of the high-pressure control solenoid valve at the actual pressure (refer to Steps S, S). The corrected driving current is passed to the high-pressure control solenoid valve, thereby ensuring appropriate and stable injection control even when there exists a variation in operational characteristics among pressure control valves.

In a fuel injection apparatus () configured so that high-pressure fuel from a common rail () is supplied to an injector () through a pressure booster (), it is discriminated whether reduction of the fuel pressure in the common rail () is necessary, the spill amount of the high-pressure fuel necessary for pressure reduction is computed when pressure reduction is discriminated to be necessary, and a control solenoid valve () is open/close controlled to spill said spill amount of the high-pressure fuel to the low-pressure side at a time point when fuel injection from the injector () is not being conducted.

Common rail fuel injection apparatus

An aluminum alloy structural member is crystalline. In producing this aluminum alloy structural member, a procedure is employed which includes forming a green compact by use of aluminum alloy having an amorphous phase, and subjecting the green compact to a powder forging technique. An aluminum alloy powder exhibiting an exotherm E smaller than 20 J/g at the time of the crystallization of the amorphous phases is used. By setting the exotherm E in such a range, cracking of the green compact due to a degassing can be avoided, even if the green compact is rapidly heated in a temperature-rising or heating course.

Process for producing structural member of aluminum alloy

A powder preform of aluminum alloy powder is subjected to a heating treatment and then to a compacting and hardening process under a pressure to produce a structural member of aluminum alloy. The aluminum alloy powder used is one having a non-equilibrium phase which shows a calorific value C in a range of C.gtoreq.10 J/g at a temperature-increasing rate of 20 K./min in a differential scanning calorimetry. In the heating treatment, the average temperature-rising rate R.sub.2 from a heat-generation starting temperature Tx (K.) of the aluminum alloy powder to Tx+A (wherein A.gtoreq.30 K.) is R.sub.2 .ltoreq.60 K./min. Thus, the change of the non-equilibrium phase in the powder preform is uniformly performed. In addition, the average temperature-increasing rate R.sub.4 from a processing temperature Tw (K.-B) in the compacting and hardening process to Tw (wherein B.gtoreq.30 K., and Tw-B&gt;Tx+A) is R.sub.4 .gtoreq.60 K./min. Thus, the oxidation of the powder preform is reliably prevented.

A heat- and abrasion-resistant aluminum alloy having a grain size of the matrix of .alpha.-aluminum in the alloy not more than 1,000 nm; a grain size of an intermetallic compounds contained in the alloy of not more than 500 nm; and 0.5 to 20% by volume of ceramic particles in the range of 1.5 to 10 .mu.m in particle size and dispersed in the alloy. By this composition, the stress concentration due to the ceramic particles is reduced. Furthermore, because the powders bind well with each other, the heat resistance and abrasion resistance are compatibly improved without decreasing toughness and ductility.

Heat- and abrasion-resistant aluminum alloy and retainer and valve

A connecting rod as a shaft clamping member includes a rod member and cap, each of which has mating faces at circumferentially opposite ends of a semi-circular recess and which are fastened to each other by bolts by matching the opposed mating faces to each other to define a crank pin hole by the two semi-circular recesses. The rod member and the cap are forgings formed from an aluminum alloy and simultaneously produced by forging powder preforms of the rod member and cap in a cavity having the desired shape of the connecting rod. After forging, the opposed mating faces have an infinite number of recesses and projections which are formed from the flow of the material during the forging and which are in a matched and fitted relation to each other. Thus, any misalignment between and in a direction parallel to the mating faces can be prevented to avoid the generation of a situation that only the rod member receives a stress. This achieves a prolongation in the life of the connecting rod of the aluminum alloy. The composition of the most desirable aluminum alloy includes, by weight, 7% .ltoreq.Fe&lt;15%, 1% &lt;Si&lt;4% and between 1% and 3% of a metal selected from Ti, Zr, Mn, Ni, Cr, V, Mg and Mm (Misch metal) with the balance Al. The preferred forging temperature is between about 550.degree. C. and 650.degree. C.

Process for producing a shaft clamping member

In a powder forging process, a heated green compact is placed in a stationary die and subjected to a press-forging carried out mainly to reduce the thickness thereof by cooperation of the stationary die with a movable die. The press-forging is performed at two pressing steps. After placement of the green compact into the concave molding portion of the stationary die, the pressing step were carried out. Thus, it is possible to produce a forged product having a high strength and a high toughness. A heated heat insulator also may be placed in the stationary die to provide a temperature-retaining effect to the green compact before and during pressing.

Powder forging process

An aluminum alloy powder or a green compact thereof is prepared, wherein: (1) the composition formula is Al.sub.100-a-b Fe.sub.a X.sub.b where a and b in atomic % are 4.0.ltoreq.a.ltoreq.6.0, 1.0.ltoreq.b.ltoreq.4.0, and where X is at least one alloy element selected from Y and Mm (mish metal); or (2) the composition formula is Al.sub.100-a-b-c Fe.sub.a Si.sub.b X.sub.c, where a, b and c in atomic % are 3.0.ltoreq.a.ltoreq.6.0, 0.5.ltoreq.b.ltoreq.3.0, and 0.5.ltoreq.c.ltoreq.3.0, and where X is at least one alloy element selected from Ti, Co, Ni, Mn and Cr, and wherein both (1) and (2) include an amorphous phase of at least 1% by volume. The aluminum alloy powder or the green compact thereof is heated at a temperature increasing at a rate of at least 80.degree. C./min. to a predetermined temperature of at least 560.degree. C. and not more than a temperature at which 10% by volume of a liquid phase is contained in the alloy powder or green compact. The aluminum alloy powder or the green compact thereof is powder forged at the predetermined temperature. As a result, an aluminum alloy superior in static strength and dynamic strength can be produced.

Powder forging method of aluminum alloy powder having high proof stress

A high strength and high toughness aluminum alloy is produced by crystallization of one of two aluminum alloy blanks: one having a metallographic structure with a volume fraction Vf of a mixed-phase texture consisting of an amorphous phase and an aluminum crystalline phase being equal to or more than 50% (Vf.gtoreq.50%), and the other having a metallographic structure with a volume fraction Vf of an amorphous single-phase texture being equal to or more than 50% (Vf.gtoreq.50%). The aluminum alloy is represented by a chemical formula:

High strength and high toughness aluminum alloy

A process for producing an aluminum alloy with high strength and toughness includes the steps of: preparing an alloy blank having a primary structure which is one selected from a single-phase structure comprised of a solid-solution phase, a single-phase structure comprised of an amorphous phase, and a mixed-phase structure comprised of a solid-solution phase and an amorphous phase, and subjecting the alloy blank to a thermal treatment to provide an aluminum alloy which has a secondary structure containing 20% or more by volume fraction Vf of chrysanthemum-like patterned phases each having a diameter of at most 5 .mu.m and comprising a solid-solution phase and an intermetallic compound phase arranged radiately.

Process for producing high strength and high toughness aluminum alloy

An offset correction apparatus comprising a turning angular velocity sensor, a vehicle speed sensor for outputting a pulsed signal every constant distance traveled by a vehicle, a stop determining unit for determining that the vehicle is at a stop, an offset calculation unit for integrating an output of the turning angular velocity sensor during a period of time that the stop of the vehicle is determined by the stop determining unit and then calculating an offset value of the output of the turning angular velocity sensor, a storage unit to store the offset value calculated by the offset calculation unit, and a heading correction unit for correcting heading data obtained from the output of the turning angular velocity sensor, with the offset value, wherein when the pulsed signal from the vehicle speed sensor disappears and the output from the turning angular velocity sensor is less than a threshold, the stop determining unit determines that the vehicle is at a stop.

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Saitama, Japan

Kenji Okamoto